Fe-based metal plate and method of manufacturing the same

ABSTRACT

On at least one surface of a base metal plate ( 1 ) of an α-γ transforming Fe or Fe alloy, a metal layer ( 2 ) containing ferrite former is formed. Next, the base metal plate ( 1 ) and the metal layer ( 2 ) are heated to an A3 point of the Fe or the Fe alloy, whereby the ferrite former are diffused into the base metal plate ( 1 ) to form an alloy region ( 1   b ) in a ferrite phase in which an accumulation degree of {200} planes is 25% or more and an accumulation degree of {222} planes is 40% or less. Next, the base metal plate ( 1 ) is heated to a temperature higher than the A3 point of the Fe or the Fe alloy, whereby the accumulation degree of the {200} planes is increased and the accumulation degree of the {222} planes is decreased while the alloy region ( 11   b ) is maintained in the ferrite phase.

This application is a national stage application of International Application No. PCT/JP2010/069102, filed Oct. 27, 2010, which claims priority to Japanese Application No. 2009-248057, filed Oct. 28, 2009, the content of which is incorporated by reference in its entirety.

TECHNICAL FIELD

The present invention relates to a Fe-based metal plate used for a magnetic core or the like and a method of manufacturing the same.

BACKGROUND ART

Silicon steel plates have been conventionally used for magnetic cores of electric motors, power generators, transformers, and the like. A silicon steel plate used for a magnetic core is required to be small in magnetic energy loss (core loss) in an alternating magnetic field and to be high in magnetic flux density in practical magnetic fields. To realize these, it is effective to increase electric resistance and to accumulate <100> axes being a direction of easy magnetization of αFe, in a direction of a used magnetic field. Especially when {100} planes of αFe are highly accumulated in a surface (rolled surface) of a silicon steel plate, <100> axes are highly accumulated in the rolled surface, so that higher magnetic flux density can be obtained. Therefore, there have been proposed various techniques aiming at the higher accumulation of {100} planes in a surface of a silicon steel plate.

However, the conventional techniques have difficulty in realizing the stable high accumulation of [100] planes in a surface of a Fe-based metal plate such as a silicon steel plate.

CITATION LIST Patent Literature

Patent Literature 1: Japanese Laid-open Patent Publication No. 01-252727

Patent Literature 2: Japanese Laid-open Patent Publication No. 05-279740

Patent Literature 3: Japanese Laid-open Patent Publication No. 2007-51338

Patent Literature 4: Japanese Laid-open Patent Publication No. 2006-144116

Patent Literature 5: Japanese National Publication of International Patent Application No. 2010-513716

SUMMARY OF INVENTION Technical Problem

It is an object of the present invention to provide a Fe-based metal plate capable of having higher magnetic flux density and a method of manufacturing the same.

Solution to Problem

(1) A method of manufacturing an Fe-based metal plate including:

-   -   forming a metal layer containing ferrite former on at least one         surface of a base metal plate of an α-γ transforming Fe or Fe         alloy;     -   next heating the base metal plate and the metal layer to an A3         point of the Fe or the Fe alloy so as to diffuse the ferrite         former into the base metal plate and form an alloy region of a         ferrite phase in which an accumulation degree of {200} planes is         25% or more and an accumulation degree of {222} planes is 40% or         less; and     -   next heating the base metal plate to a temperature equal to or         higher than the A3 point of the Fe or the Fe alloy so as to         increase the accumulation degree of the {200} planes and         decrease the accumulation degree of the {222} planes while         maintaining the alloy region of the ferrite phase.

(2) The method of manufacturing an Fe-based metal plate according to (1), including, after the increasing the accumulation degree of the {200}planes and the decreasing the accumulation degree of the {222} planes, cooling the base metal plate to a temperature lower than the A3 point of the Fe or the Fe alloy so as to transform an unalloyed region in the base metal plate from an austenitic phase to a ferrite phase, further increase the accumulation degree of the {200} planes and further decrease the accumulation degree of the {222} planes.

(3) The method of manufacturing an Fe-based metal plate according to (1) or (2), wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, the accumulation degree of the {200} planes is increased to 30% or more and the accumulation degree of the {222} planes is decreased to 30% or less.

(4) The method of manufacturing an Fe-based metal plate according to (1) or (2), wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, the accumulation degree of the {200} planes is increased to 50% or more and the accumulation degree of the {222} planes is decreased to 15% or less.

(5) The method of manufacturing an Fe-based metal plate according to any one of (1) to (4), wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, the ferrite former contained in the metal layer are all diffused into the base metal plate.

(6) The method of manufacturing an Fe-based metal plate according to any one of (1) to (5), wherein the ferrite former are at least one kind selected from a group consisting of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ti, V, W, and Zn.

(7) The method of manufacturing an Fe-based metal plate according to any one of (1) to (6), wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, an area ratio of a ferrite single phase region to the metal plate in a cross section in a thickness direction is made to 1% or more.

(8) The method of manufacturing an Fe-based metal plate according to any one of (1) to (7), wherein as the base metal plate, used is one in which a working strain is brought about and in which dislocation density is not less than 1×10¹⁵ m/m³ nor more than 1×10¹⁷ m/m³.

(9) The method of manufacturing an Fe-based metal plate according to any one of (1) to (7), wherein as the base metal plate, used is one in which a working strain is brought about by cold rolling in which rolling reduction ratio is not less than 97% nor more than 99.99%.

(10) The method of manufacturing an Fe-based metal plate according to any one of (1) to (7), wherein as the base metal plate, used is one in which a working strain is brought about by shot blasting.

(11) The method of manufacturing an Fe-based metal plate according to any one of (1) to (7), wherein as the base metal plate, used is one in which a working strain is brought about by cold rolling in which rolling reduction ratio is not less than 50% nor more than 99.99% and shot blasting.

(12) The method of manufacturing an Fe-based metal plate according to any one of (1) to (7), wherein as the base metal plate, used is one in which a shear strain of 0.2 or more is brought about by cold rolling.

(13) The method of manufacturing an Fe-based metal plate according to any one of (1) to (7), wherein as the base metal plate, used is one in which a shear strain of 0.1 or more is brought about by cold rolling and a working strain is brought about by shot blasting.

(14) The method of manufacturing an Fe-based metal plate according to any one of (1) to (13), wherein a thickness of the base metal plate is not less than 10 μm nor more than 5 mm.

(15) A Fe-based metal plate, containing ferrite former, wherein, in a surface, an accumulation degree of {200} planes in a ferrite phase is 30% or more and an accumulation degree of {222} planes in the ferrite phase is 30% or less.

(16) The Fe-based metal plate according to (15), being formed by diffusion of the ferrite former from a surface to an inner part of an α-γ transforming Fe or Fe alloy plate.

(17) The Fe-based metal plate according to (15) or (16), including, on the surface, a metal layer containing the ferrite former.

(18) The Fe-based metal plate according to any one of (15) to (17), wherein the accumulation degree of the {200} planes is 50% or more and the accumulation degree of the {222} planes is 15% or less.

(19) The Fe-based metal plate according to any one of (15) to (18), wherein the ferrite former are at least one kind selected from a group consisting of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ti, V, W, and Zn.

(20) The Fe-based metal plate according to any one of (15) to (19), including a 1% ferrite single phase region or more in terms of an area ratio in a thicknesswise cross section of the metal plate.

The accumulation degree of the {200} planes in the ferrite phase is expressed by an expression (1) and the accumulation degree of the {222} planes in the ferrite phase is expressed by an expression (2). accumulation degree of {200}planes=[{i(200)/I(200)}/Σ{i(hkl)/I(hkl)}]×100  (1) accumulation degree of {222}planes=[{i(222)/I(222)}/Σ{i(hkl)/I(hkl)}]×100  (2)

Here, i(hkl) is actually measured integrated intensity of {hkl} planes in the surface of the Fe-based metal plate or the base metal plate, and I(hkl) is theoretical integrated intensity of {hkl} planes in a sample having random orientation. As the (hkl) planes, used are, for examples, 11 kinds of {110}, {200}, {211}, {310}, {222}, {321}, {411}, {420}, {332}, {521}, and {442} planes.

Advantageous Effects of Invention

According to the present invention, it is possible to obtain a Fe-based metal plate in which an accumulation degree of {200} planes in a ferrite phase is high and an accumulation degree of {222} planes in the ferrite phase is low, and to improve magnetic flux density.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1A is a cross-sectional view showing a basic principle of the present invention.

FIG. 1B which continues from FIG. 1A, is a cross-sectional view showing the basic principle of the present invention.

FIG. 1C, which continues from FIG. 1B, is a cross-sectional view showing the basic principle of the present invention.

FIG. 1D, which continues from FIG. 1C, is a cross-sectional view showing the basic principle of the present invention.

FIG. 1E, which continues from FIG. 1D, is a cross-sectional view showing the basic principle of the present invention.

FIG. 2A is a cross-sectional view showing a method of manufacturing a Fe-based metal plate according to a first embodiment.

FIG. 2B, which continues from FIG. 2A, is a cross-sectional view showing the method of manufacturing the Fe-based metal plate.

FIG. 2C, which continues from FIG. 2B, is a cross-sectional view showing the method of manufacturing the Fe-based metal plate.

FIG. 2D, which continues from FIG. 2C, is a cross-sectional view showing the method of manufacturing the Fe-based metal plate.

FIG. 3 is a cross-sectional view showing a method of manufacturing a Fe-based metal plate according to a second embodiment.

FIG. 4 is a cross-sectional view showing a method of manufacturing a Fe-based metal plate according to a third embodiment.

DESCRIPTION OF EMBODIMENTS

(Basic Principle of Present Invention)

First, a basic principle of the present invention will be described. FIG. 1A to FIG. 1E are cross-sectional views showing the basic principle of the present invention.

In the present invention, for example, as illustrated in FIG. 1A, a metal layer 2 containing ferrite former is formed on at least one surface of a base metal plate 1 composed of an α-γ transforming Fe-based metal (Fe or Fe alloy). As the base metal plate 1, for example, pure iron plate cold-rolled with a very high rolling reduction ratio of about 99.8% is used. Further, as the metal layer 2, an Al layer is formed, for example.

Next, the base metal plate 1 and the metal layer 2 are heated to the A3 point of the material (pure iron) of the base metal plate 1. During the heating, as illustrated in FIG. 1B, Al being the ferrite former in the metal layer 2 is diffused into the base metal plate 1, so that an alloy region 1 b in a ferrite phase (α phase) is formed. The remainder of the base metal plate 1 is an unalloyed region 1 a in the α phase until an instant immediately before the A3 point is reached. In accordance with the heating, recrystallization occurs in the alloy region 1 b and the unalloyed region 1 a. Further, since a large strain has been generated due to the cold rolling, planes parallel to a surface of the base metal plate 1 (rolled surface), of grains generated by the recrystallization are likely to be oriented in {100}. Therefore, many grains whose planes parallel to the rolled surface are oriented in {100} are generated both in the alloy region 1 b and the unalloyed region 1 a. Here, important points of the present invention are that, by the instant before the temperature reaches the A3 point, α-phase grains oriented in {100} are contained in the alloy region 1 b due to the diffusion of Al being the ferrite former, and that the alloy region 1 b has the α single phase alloy composition.

Thereafter, the base metal plate 1 and the metal layer 2 are further heated to a temperature equal to or higher than the A3 point of the pure iron. As a result, as illustrated in FIG. 1C, the unalloyed region 1 a composed of the pure iron is γ-transformed to become an austenitic phase (γ phase), while the alloy region 1 b containing Al being the ferrite former is maintained in the α phase. Even at the temperature equal to or higher than the A3 point, the α-phase grains oriented in {100}, which are formed at lower than the A3 point, do not undergo the γ-transformation and their crystal orientation is maintained. Further, in the alloy region 1 b, grains 3 whose planes parallel to the rolled surface are oriented in {100} predominantly grow. Along with the growth of the {100} grains, grains oriented in other directions vanish. For example, grains whose planes parallel to the rolled surface are oriented in {111} decrease. Therefore, in the alloy region 1 b, the accumulation degree of {200} planes in the α phase increases and the accumulation degree of {222} planes in the α phase decreases.

Then, when the base metal plate 1 and the metal layer 2 are kept at the temperature equal to or higher than the A3 point of the pure iron, Al in the metal layer 2 further diffuses into the base metal plate 1, and as illustrated in FIG. 1D, the alloy region 1 b in the α phase expands. That is, in accordance with the diffusion of Al being the ferrite former, part of the unalloyed region 1 a in the γ phase changes to the alloy region 1 b in the α phase. At the time of this change, since the alloy region 1 b being a region adjacent to a metal layer 2 side of the region where the change occurs has already been oriented in {100}, the region where the change occurs takes over the crystal orientation of the alloy region 1 b to be oriented in {100}. As a result, the grains 3 whose planes parallel to the rolled surface are oriented in {100} further grow. Then, along with the growth of the grains 3, the accumulation degree of the {200} planes in the α phase further increases and the accumulation degree of the {222} planes in the α phase further decreases.

Subsequently, the base metal plate 1 is cooled to a temperature lower than the A3 point of the pure iron. As a result, as illustrated in FIG. 1E, the unalloyed region 1 a composed of the pure iron is α-transformed to the α phase. At the time of the phase transformation as well, since the alloy region 1 b being the region adjacent to the metal layer 2 side of the region where the phase transformation occurs has already been oriented in {100}, the region where the phase transformation occurs takes over the crystal orientation of the alloy region 1 b to be oriented in {100}. As a result, the grains 3 whose planes parallel to the rolled surface are oriented in {100} further grow. Then, along with the growth of the grains 3, the accumulation degree of the {200} planes in the α phase further increases and the accumulation degree of the {222} planes in the α phase further decreases. That is, a high accumulation degree of the {200} planes in the α phase is obtained also in the unalloyed region 1 a.

Incidentally, when the metal layer 2 is thick and the keeping time of the temperature equal to or higher than the A3 point is long, Al sufficiently diffuses and the unalloyed region 1 a sometimes disappears before the temperature of the base metal plate 1 reaches lower than the A3 point at the time of the cooling. In this case, the phase transformation of the unalloyed region 1 a does not occur, and since the whole region has become the alloy region 1 b, the state at the start of the cooling is maintained.

Therefore, in the Fe-based metal plate (Fe or Fe alloy plate) manufactured through these processes, the accumulation degree of the {200} planes in the α phase is extremely high and the accumulation degree of the {222} planes in the α phase is extremely low. Therefore, high magnetic flux density is obtained.

Here, conditions in the present invention will be described.

“Base Metal Plate”

As a material of the base metal plate, an α-γ transforming Fe-based metal (Fe or Fe alloy) is used. The Fe-based metal contains, for example, 70 mass % Fe or more. Further, the α-γ transformation series is, for example, a component series which has the A3 point within a range of about 600° C. to 1000° C., and which has an α phase as its main phase at lower than the A3 point and has a γ phase as its main phase at the A3 point or higher. Here, the main phase refers to a phase whose volume ratio is over 50%. The use of the α-γ transforming Fe-based metal makes it possible to form a region having an α single phase composition in accordance with the diffusion and alloying of a ferrite former. Examples of the α-γ transforming Fe-based metal may be pure iron, low-carbon steel, and the like. For example, usable is pure iron whose C content is 1 mass ppm to 0.2 mass %, with the balance being Fe and inevitable impurities. Also usable is silicon steel composed of an α-γ transforming component whose basic components are C with a 0.1 mass % content or less and Si with a 0.1 mass % to 2.5 mass % content. Further, any of these to which various kinds of elements are added may also be used. Examples of the various elements are Mn, Ni, Cr, Al, Mo, W, V, Ti, Nb, B, Cu, Co, Zr, Y, Hf, La, Ce, N, O, P, S, and so on. However, it is preferable that Mn and Ni are not contained because they may involve a risk of lowering magnetic flux density.

As the base metal plate, one in which a strain is brought about is used, for example. This is intended to generate many grains whose planes parallel to the rolled surface are oriented in {100}, at the time of the recrystallization of the base metal plate, thereby improving the accumulation degree of the {200} planes in the α phase. For example, it is preferable to bring about a working strain with which dislocation density becomes not less than 1×10¹⁵ m/m³ nor more than 1×10¹⁷ m/m³. A method for generating such a strain is not particularly limited, but, for example, it is preferable to apply cold rolling with a high rolling reduction ratio, especially with a rolling reduction ratio of not less than 97% nor more than 99.99%. Alternatively, a shear strain of 0.2 or more may be generated by cold rolling. It is possible to generate the shear strain by, for example, rotating upper and lower reduction rolls at different speeds at the time of the cold rolling. In this case, the larger a difference in the rotation speed between the upper and lower reduction rolls, the larger the shear strain. The shear strain may be calculated from diameters of the reduction rolls and a difference in rotation speed therebetween.

The strain need not exist all along the thickness direction of the base metal plate, and the strain only needs to exist in a portion where the formation of the alloyed region starts, that is, in a surface layer portion of the base metal plate. Therefore, the working strain may be brought about by shot blasting, or the generation of the working strain or the generation of the shear strain by the cold rolling may be combined with the generation of the working strain by the shot blasting. When the cold rolling and the shot blasting are combined, a rolling reduction ratio of the cold rolling may be not less than 50% nor more than 99.99%. When the generation of the shear strain and the shot blasting are combined, the shear strain may be 0.1 or more. When the working strain is brought about by the shot blasting, it is possible to make the orientation of the {100} planes of the grains uniform in planes parallel to the surface of the Fe-based metal plate.

As the base metal plate, one in which a texture oriented in {100} is formed in the surface layer portion in advance may be used, for example. In this case as well, in the alloy region, it is possible to increase the accumulation degree of the {200} planes in the α phase and decrease the accumulation degree of the {222} planes in the α phase. It is possible to obtain such a base metal plate by, for example, subjecting a metal plate including a large strain to recrystallization annealing.

Though details will be described later, a base metal plate may be used in which an α-phase alloy region where the accumulation degree of the {200} planes in the α phase is 25% or more and the accumulation degree of the {222} planes in the α phase is 40% or less is formed at the time of the heating to the A3 point.

A thickness of the base metal plate is preferably not less than 10 μm nor more than 5 mm, for example. As will be described later, a thickness of the Fe-based metal plate is preferably more than 10 μm and 6 mm or less. Considering that the metal layer is formed, when the thickness of the base metal plate is not less than 10 μm nor more than 5 mm, the thickness of the Fe-based metal plate may be easily more than 10 μm and 6 mm or less.

“Ferrite former and Metal Layer”

As the ferrite former, Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ta, Ti, V, W, Zn, or the like is preferably used. The use of any of these elements facilitates forming the region having the α single phase composition and makes it possible to efficiently enhance the accumulation degree of the {200} planes in the α phase.

A method of forming the metal layer containing the ferrite former is not particularly limited, and examples thereof may be plating methods such as a hot dipping method and an electrolytic plating method, dry process methods such as a PVD (physical vapor deposition) method and a CVD (chemical vapor deposition) method, a rolling clad method, powder coating, and so on. Among them, the plating method and the rolling clad method are preferable especially when the method is industrially implemented. This is because they may easily and efficiently form the metal layer.

A thickness of the metal layer is preferably not less than 0.05 μm nor more than 1000 μm. When the thickness of the metal layer is less than 0.05 μm, it may be difficult to sufficiently form the alloy region and it is not sometimes possible to obtain the sufficient accumulation degree of the {200} planes in the α phase. Further, when the thickness of the metal layer is over 1000 μm, the metal layer sometimes remains thickly after the cooling to lower than the A3 point and a high magnetic property cannot be sometimes obtained.

“Ratio of Alloying of Metal Layer”

In the metal layer, a ratio of its portion alloyed with the base metal plate is preferably 10% or more in the thickness direction. When the ratio is less than 10%, it may be difficult to sufficiently form the alloy region and it is not sometimes possible to obtain the sufficient accumulation degree of the {200} planes in the α phase. Incidentally, the ratio (alloying ratio) may be expressed by an expression (3), where S0 is an area of the metal layer before the heating in a cross section perpendicular to the surface of the base metal plate and S is an area of the metal layer after the heating and the cooling. alloying ratio=((S0−S)/S0)×100  (3)

“Ratio of α Single Phase Region”

The region having the α single phase composition as a result of the alloying of the ferrite former and Fe has mainly a ferrite single phase (α single phase region) after the heating and the cooling. On the other hand, the unalloyed region in the base metal plate has mainly the α-γ transformed region after the heating and the cooling. Therefore, the α single phase region is substantially equivalent to the alloyed region. A ratio of the α single phase region to the base metal plate is preferably 1% or more in terms of an area ratio in a cross section in the thickness direction. When the ratio is less than 1%, the alloy region is not sufficiently formed and the sufficient accumulation degree of the {200} planes in the α phase is not sometimes obtained. In order to obtain a higher accumulation degree of the {200} planes in the α phase, the ratio is preferably 5% or more.

Further, in the α single phase region where the ferrite former is alloyed, since electric resistance is high, an effect of improving a core loss characteristic is obtained. As a desirable condition under which this effect is obtained, the ratio of the α single phase region to the metal plate in the thickness direction is 1% or more. When it is less than 1%, the accumulation degree of the {200} planes is not sufficiently high and it may be difficult to obtain an excellent core loss characteristic.

In order to obtain a more excellent core loss characteristic, the ratio of the α single phase region to the metal plate in the thickness direction is desirably not less than 5% nor more than 80%. When it is 5% or more, the accumulation degree of the {200} planes is remarkably high and the core loss characteristic accordingly improves. When it is 80% or less, the electric resistance of the α single phase region is still higher and the core loss is remarkably lower due to a synergistic effect with the effect of improving the accumulation degree of the {200} planes.

Here, the ratio of the α single phase region may be expressed by an expression (4), where T0 is an area of the cross section perpendicular to the surface of the Fe-based metal plate after the heating and the cooling and T is an area of the α single phase region after the heating and the cooling. Here, when Al is used as the ferrite former is, for example, the α single phase region is a region where the Al content is not less than 0.9 mass % nor more than 10 mass %. This range differs depending on the kind of the ferrite former and is a range shown in a Fe-based alloy phase diagram or the like. ratio of α single phase region=(T/T0)×100  (4)

“Plane Accumulation Degrees in Fe-based Metal Plate”

The accumulation degree of the {200} planes in the α phase in the surface (rolled surface) of the Fe-based metal plate is 30% or more. When the accumulation degree of the {200} planes in the α phase is less than 30%, it may be not possible to obtain sufficiently high magnetic flux density. In order to obtain higher magnetic flux density, the accumulation degree of the {200} planes in the α phase is preferably 50% or more. However, when the accumulation degree of the {200} planes in the α phase is over 99%, the magnetic flux density saturates. Further, making the accumulation degree of the {200} planes in the α phase higher than 99% is difficult in view of manufacture. Therefore, the accumulation degree of the {200} planes in the α phase is preferably 99% or less, more preferably 95% or less.

The accumulation degree of the {222} planes in the α phase in the surface (rolled surface) of the Fe-based metal plate is 30% or less. When the accumulation degree of the {222} planes in the α phase is over 30%, it is not possible to obtain sufficiently high magnetic flux density. In order to obtain higher magnetic flux density, the accumulation degree of the {222} planes in the α phase is preferably 15% or less. However, when the accumulation degree of the {222} planes in the α phase is less than 0.01%, the magnetic flux density saturates. Further, making the accumulation degree of the {222} planes in the α phase less than 0.01% may be difficult in view of manufacture. Therefore, the accumulation degree of the {222} planes in the α phase is preferably 0.01% or more.

These plane accumulation degrees may be measured by X-ray diffraction using a MoKα ray. To be in more detail, in α phase crystals, integrated intensities of eleven orientation planes ({110}, {200}, {211}, {310}, {222}, {321}, {411}, {420}, {332}, {521}, and {442}) parallel to its surface is measured for each sample, each measurement value is divided by theoretical integrated intensity of the sample having random orientation, and thereafter, a ratio of the intensity of {200} or {222} is found in percentage.

At this time, the accumulation degree of the {200} planes in the α phase is expressed by an expression (1) and the accumulation degree of the {222} planes in the α phase is expressed by an expression (2), for example. accumulation degree of {200}planes=[{i(200)/I(200)}/Σ{i(hkl)/I(hkl)}]×100  (1) accumulation degree of {222}planes=[{i(222)/I(222)}/Σ{i(hkl)/I(hkl)}]×100  (2)

Here, i(hkl) is actually measured integrated intensity of {hkl} planes in the surface of the Fe-based metal plate or the base metal plate, and I(hkl) is theoretical integrated intensity of the {hkl} planes in the sample having random orientation. Incidentally, instead of the theoretical integrated intensity of the sample having the random orientation, results of actual measurement using the sample (actually measured values) may be used.

Incidentally, only making Al and Si contained in the steel plate for the purpose of reducing the core loss accompanying the increase in the electric resistance has difficulty in sufficiently reducing the core loss due to the influence of magnetostriction. When the α phase plane accumulation degree is within the aforesaid range, a remarkably good core loss can be obtained. This is thought to be because a difference in magnetostriction among grains is extremely small. This effect is distinguished especially when there are many columnar crystals extending in a direction perpendicular to the surface of the Fe-based metal plate.

“Thickness of Fe-Based Metal Plate”

The thickness of the Fe-based metal plate is preferably over 10 μm and 6 mm or less. When the thickness is 10 μm or less, very many Fe-based metal plates are used when they are stacked to form a magnetic core, which results in much gap between the Fe-based metal plates accompanying the stacking. As a result, high magnetic flux density may be difficult to obtain. Further, when the thickness is over 6 mm, it may be difficult to form a wide alloyed region and it is difficult to sufficiently improve the accumulation degree of the {200} planes in the α phase.

“State of Metal Layer after Heating and Cooling”

In accordance with the heating and the cooling, the whole metal layer may be diffused into the base metal plate or part of the metal layer may remain on a front surface and/or a rear surface of the base metal plate. Further, when part of the metal layer remains after the heating and the cooling, the remaining part may be removed by etching or the like. The metal layer remaining on the front surface and/or the rear surface of the base metal plate may enhance chemical stability of the surface layer portion of the Fe-based metal plate to improve corrosion resistance depending on its composition. When the metal layer is made to remain for the purpose of improving corrosion resistance, its thickness is preferably not more than 0.01 μm nor less than 500 μm. When the thickness is less than 0.01 μm, the metal layer may suffer a defect such as breakage, which is likely to make the core loss unstable. When the thickness is over 500 μm, the metal layer may suffer a defect such as exfoliation, which is likely to make corrosion resistance unstable.

“Transition of α Phase Plane Accumulation Degrees”

In heating the base metal plate and the metal layer, the accumulation degree of the {200} planes in the α phase is 25% or more and the accumulation degree of the {222} planes in the α phase is 40% or less in the alloy region when the A3 point is reached. When the accumulation degree of the {200} planes in the α phase is less than 25%, and when the accumulation degree of the {222} planes in the α phase is over 40%, it may be difficult to set the accumulation degree of the {222} planes in the α phase to 30% or less and the accumulation degree of the {200} planes in the α phase to 30% or more in the Fe-based metal plate. Further, the accumulation degree of the {200} planes in the α phase is preferably 50% or less and the accumulation degree of the {222} planes in the α phase is preferably 1% or more, in the alloy region when the A3 point is reached. When the accumulation degree of the {200} planes in the α phase is over 50%, and when the accumulation degree of the {222} planes in the α phase is less than 1%, the magnetic flux density of the Fe-based metal plate is likely to saturate. Further, in view of manufacture, it may be difficult to set the accumulation degree of the {200} planes in the α phase to more than 50% and to set the accumulation degree of the {222} planes in the α phase to less than 1%.

Further, in heating and cooling the base metal plate and the metal layer, it is preferable that the accumulation degree of the {200} planes in the α phase is 30% or more and the accumulation degree of the {222} planes in the α phase is 30% or less, in the alloy region when the cooling is started. When the accumulation degree of the {200} planes in the α phase is less than 30%, and when the accumulation degree of the {222} planes in the α phase is over 30%, it is likely to be difficult to set the accumulation degree of the {222} planes in the α phase to 30% or less and set the accumulation degree of the {200} planes in the α phase to 30% or more, in the Fe-based metal plate. Further, when the cooling is started, it is preferable that the accumulation degree of the {200} planes in the α phase is 99% or less and the accumulation degree of the {222} planes in the α phase is 0.01% or more, in the alloy region. When the accumulation degree of the {200} planes in the α phase is over 99%, and when the accumulation degree of the {222} planes in the α phase is less than 0.01%, the magnetic flux density of the Fe-based metal plate is likely to saturate. Further, in view of manufacture, it may be difficult to set the accumulation degree of the {200} planes in the α phase to over 99% and to set the accumulation degree of the {222} planes in the α phase to less than 0.01%.

Further, it is more preferable that the accumulation degree of the {200} planes in the α phase is 50% or more and the accumulation degree of the {222} planes in the α phase is 15% or less, in the alloy region when the cooling is started. Further, the accumulation degree of the {200} planes in the α phase is more preferably 95% or less in the alloy region when the cooling is started.

When an unalloyed region exists at the start of the cooling, the unalloyed region transforms from the γ phase to the α phase at the A3 point as described above. In the unalloyed region after the transformation, it is also preferable that the accumulation degree of the {200} planes in the α phase is not less than 30% nor more than 99%. When the accumulation degree of the {200} planes in the α phase is less than 30%, it is likely to be difficult to set the accumulation degree of the {222} planes in the α phase of the Fe-based metal plate to 30% or less. When the accumulation degree of the {200} planes in the α phase is over 99%, the magnetic flux density of the Fe-based metal plate is likely to saturate. Further, in view of manufacture, it may be difficult to set the accumulation degree of the {200} planes in the α phase to over 99%.

“Temperature Increasing Rate and Cooling Rate”

Heating up to the A3 point temperature and heating up to the temperature equal to or higher than the A3 point may be continuously performed, and temperature increasing rates thereof are preferably not less than 0.1° C./sec nor more than 500° C./sec. When the temperature increasing rate is within this range, grains whose planes parallel to the surface of the base metal plate are oriented in {100} are likely to be generated at the time of the recrystallization.

A keeping temperature after the temperature increase is preferably not lower than A3 point nor higher than 1300° C. When the temperature is kept at over 1300° C., the effect saturates. Further, the keeping time is not particularly limited, and the cooling may be started immediately after a predetermined temperature is reached. Further, when the temperature is kept for 36000 sec (ten hours), it is possible to fully diffuse the ferrite former into the metal layer.

A cooling rate at the time of the cooling to the temperature lower than A3 point is preferably not less than 0.1° C./sec nor more than 500° C./sec. The cooling with the temperature range facilitates enhancing the accumulation degree of the {200} planes in the α phase.

An atmosphere at the time of the temperature increase and an atmosphere at the time of the cooling are not particularly limited, and in order to suppress oxidization of the base metal plate and the metal layer, a non-oxidizing atmosphere is preferable. For example, an atmosphere of mixed gas of inert gas such as Ar gas or N₂ gas and reducing gas such as H₂ gas is preferable. Further, the temperature increase and/or the cooling may be performed under vacuum.

(First Embodiment)

Next, a first embodiment will be described. FIG. 2A to FIG. 2D are cross-sectional views showing a method of manufacturing a Fe-based metal plate according to the first embodiment of the present invention in order of processes.

In the first embodiment, as illustrated in FIG. 2A, metal layers 12 containing Al are first formed on a front surface and a rear surface of a base metal plate 11 composed of pure iron and having strain.

Next, the base metal plate 11 and the metal layers 12 are heated to the A3 point of the pure iron (911° C.) so that ferrite former in the metal layers 12 are diffused into the base metal plate 11, whereby alloy regions in an α phase are formed. The remainder of the base metal plate 11 is an unalloyed region in the α phase until an instant immediately before the A3 point is reached. In accordance with the heating, recrystallization occurs in the base metal plate 11. Further, because of the strain in the base metal plate 11, planes parallel to a surface (rolled surface) of the base metal plate 11, of grains generated by the recrystallization are likely to be oriented in {100}. Therefore, many grains whose planes parallel to the rolled surface are oriented in {100} are generated in the base metal plate 11.

Thereafter, the base metal plate 11 and the metal layers 12 are further heated up to a temperature equal to or higher than the A3 point of the pure iron. As a result, as illustrated in FIG. 2B, the unalloyed region 11 a comprised of the α-γ transforming pure iron undergoes γ-transformation to become a γ phase, while the alloy regions 11 b containing Al being the ferrite former are maintained in the α phase. Further, Al in the metal layers 12 further diffuses into the base metal plate 11, so that the alloy regions 11 b in the α phase expand. Further, in the alloy regions 11 b, since the grains 13 whose planes parallel to the rolled surface are oriented in {100} predominantly grow, an accumulation degree of {200} planes in the α phase increases and an accumulation degree of {222} planes in the α phase decreases, in the alloy regions 11 b.

Then, the base metal plate 11 and the metal layers 12 are kept at the temperature equal to or higher than the A3 point of the pure iron, and Al in the metal layers 12 further diffuses into the base metal plate 11, and as illustrated in FIG. 2C, the alloy regions 11 b in the α phase expand. That is, in accordance with the diffusion of Al, part of the unalloyed region 11 a in the γ phase changes to the alloy regions 11 b in the α phase. At the time of the change, since the alloy regions 11 b, which are adjacent to metal layer 12 sides of the regions undergoing the change, have been already oriented in {100}, the regions undergoing the change take over the crystal orientation of the alloy regions 11 b to be oriented in {100}. As a result, the grains 13 whose planes parallel to the rolled surface are oriented in {100} further grow. Then, along with the growth of the grains 13, grains oriented in other directions vanish. For example, grains whose planes parallel to the rolled surface are oriented in {111} decrease. As a result, the accumulation degree of the {200} planes in the α phase further increases and the accumulation degree of the {222} planes in the α phase further decreases.

Subsequently, the base metal plate 11 is cooled to a temperature lower than the A3 point of the pure iron. As a result, as illustrated in FIG. 2D, the unalloyed region 11 a undergoes α-transformation to become the α phase. At the time of the phase transformation as well, since the alloy regions 11 b, which are adjacent to the metal layer 12 sides of the regions undergoing the phase transformation, have already been oriented in {100}, the regions undergoing the phase transformation take over the crystal orientation of the alloy regions 11 b to be oriented in {100}. As a result, the grains 13 further grow. Then, along with the growth of the grains 13, the grains oriented in the other directions further vanish. As a result, the accumulation degree of the {200} planes in the α phase further increases and the accumulation degree of the {222} planes in the α phase further decreases. That is, a high accumulation degree of the {200} planes in the α phase is also obtained in the unalloyed region 11 a.

Thereafter, insulating films are formed on the surfaces of the metal layers 12. In this manner, the Fe-based metal plate may be manufactured. Incidentally, the metal layers 12 may be removed before the formation of the insulating films.

(Second Embodiment)

Next, a second embodiment will be described. FIG. 3 is a cross-sectional view showing a method of manufacturing a Fe-based metal plate according to the second embodiment of the present invention.

In the second embodiment, in the same manner as that of the first embodiment, the processes up to the heating of the base metal plate 11 and the metal layers 12 to a temperature of the A3 point of pure iron are performed (FIG. 2A to FIG. 2B). Then, the base metal plate 11 and the metal layers 12 are kept at a temperature equal to or higher than the A3 point. At this time, the temperature is kept for a longer time or the keeping temperature is made higher than in the first embodiment, and as illustrated in FIG. 3, Al in the metal layers 12 is all diffused into the base metal plate 11. Further, grains 13 are greatly gown, and almost all the grains oriented in directions other than {100} are made to vanish, so that the whole base metal plate 11 is turned into the α phase.

Thereafter, the cooling of the base metal plate 11 and the formation of the insulating films are performed in the same manner as that in the first embodiment. In this manner, the Fe-based metal plate may be manufactured.

(Third Embodiment)

Next, a third embodiment will be described. FIG. 4 is a cross-sectional view showing a method of manufacturing a Fe-based metal plate according to the third embodiment of the present invention.

In the third embodiment, in the same manner as that in the first embodiment, the processes up to the heating of the base metal plate 11 and the metal layers 12 to a temperature of the A3 point of pure iron are performed (FIG. 2A to FIG. 2B). Here, the metal layers 12 are formed thicker than in the first embodiment. Then, the base metal plate 11 and the metal layers 12 are kept at a temperature equal to or higher than the A3 point of the pure iron. At this time, the temperature is kept for a longer time or the keeping temperature is made higher than in the first embodiment, and as illustrated in FIG. 4, Al is diffused into the whole base metal plate 11. That is, the whole base metal plate 11 is turned into the alloy region 11 b.

Thereafter, the cooling of the base metal plate 11 and the formation of the insulating films are performed in the same manner as that in the first embodiment. In this manner, the Fe-based metal plate may be manufactured.

EXAMPLE First Experiment

In a first experiment, correlations between 27 kinds of manufacturing conditions (condition No. 1-1 to condition No. 1-27) and an accumulation degree of {200} planes and an accumulation degree of {222} planes were studied.

Base metal plates used in the first experiment contained C: 0.0001 mass %, Si: 0.0001 mass %, Al: 0.0002 mass %, and inevitable impurities, with the balance being Fe. The base metal plates were fabricated in such manner that an ingot was produced by vacuum melting, followed by hot rolling and cold rolling. In the hot rolling, the ingot with a 230 mm thickness heated to 1000° C. was thinned to a 50 mm thickness, whereby a hot-rolled plate was obtained. Thereafter, plate materials different in thickness were cut out from the hot-rolled plate by machining, and the plate materials were subjected to the cold rolling with rolling reduction ratios listed in Table 1. Thicknesses of the obtained base metal plates (cold-rolled plates) are listed in Table 1.

Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope. In this measurement, a thin film sample with which a texture of a cross section perpendicular to a surface of each of the base metal plates could be observed was fabricated, and a region from the surface to a thickness-direction center of the base metal plate was observed. Then, texture photographs were taken at several places in this region, and the dislocation density was found from the number of dislocation lines. Average values of the obtained dislocation densities are listed in Table 1.

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 20% to 26% range and the accumulation degree of the {222} planes in the α phase was an 18% to 24% range, in each of the base metal plates.

Thereafter, Al layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by an ion plating (IP) method or a hot dipping method, except in the condition No. 1-1. Thickness of each of the metal layers (total thickness on the both surfaces) is listed in Table 1. The metal layers whose thickness (total thickness on the both surfaces) was 0.01 μm to 0.4 μm were formed by the IP method, and the metal layers whose thickness (total thickness on the both surfaces) was 13 μm to 150 μm were formed by the hot dipping method. The total thickness on the both surfaces is a value obtained by summing the thickness measured on one surface and the thickness measured on the other surface.

Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions. A gold image furnace was used for the heat treatment, and the temperature increasing rate and the keeping time were variously controlled by program control. The temperature increase and the temperature keeping were performed in an atmosphere vacuumed to 10⁻³ Pa level. At the time of cooling at a cooling rate of 1° C./sec or lower, temperature control was performed in vacuum by furnace output control. At the time of cooling at a cooling rate of 10° C./sec or more, Ar gas was introduced and the cooling rate was controlled by the adjustment of its flow rate. In this manner, 27 kinds of Fe-based metal plates were manufactured.

Further, in the heat treatment, three samples were prepared per condition, and the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment.

One of the samples (first sample) was heated from room temperature to the A3 point (911° C.) at each temperature increasing rate listed in Table 1, and was cooled to room temperature immediately at a cooling rate of 100° C./sec, except in the condition No. 1-2. In the condition No. 1-2, the sample was heated to 900° C. and was immediately cooled to room temperature at a cooling rate of 100° C./sec. Then, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured. Results of these are listed in Table 1.

Another sample (second sample) was heated from room temperature to 1000° C. at the same temperature increasing rate as that for the first sample, was kept at 1000° C. for each time listed in Table 1, and was cooled to room temperature at a cooling rate of 100° C./sec, except in No. 1-2. In the condition No. 1-2, the sample was heated to 900° C., was kept at 900° C. for the time listed in Table 1, and was cooled to room temperature at a cooling rate of 100° C./sec. Then, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured. Results of these are listed in Table 1.

The other one sample (third sample) was heated and was kept at 900° C. or 1000° C. similarly to the second sample, and thereafter was cooled to room temperature at each cooling rate listed in Table 1. Then, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured. Results of these are listed in Table 1. In the measurement of the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase in the third samples, when the whole Fe-based alloy plate was alloyed, a thickness-direction center region was an evaluation target, and when an unalloyed region existed in the Fe-based alloy plate, the unalloyed region was an evaluation target. Distances of these evaluation targets from the surface of the Fe-based alloy plate are listed in Table 1 (column of “distance”). In fabricating test pieces, portions above the evaluation targets were removed so that the evaluation targets were exposed.

TABLE 1 FIRST SAMPLE BASE METAL PLATE MEA- ACCUMU- ACCUMU- REDUC- DISLOCA- METAL LAYER SURED LATION LATION CONDI- TION TION THICK- THICK- HEATING TEMPER- DEGREE OF DEGREE OF TION RATIO DENSITY NESS NESS RATE ATURE [200] PLANE [222] PLANE No. (%) (m/m³) (μm) ELEMTNT (μm) CCA) (° C.) (%) (%) COMPARATIVE 1-1 97.6 2 × 10¹⁰ 150 NONE 10 911 22 12 EXAMPLE 1-2 97.6 2 × 10¹⁶ 150 Al 20 10 900 23 12 EXAMPLE 1-3 95 6 × 10¹⁴ 150 Al 20 10 911 27 11 OF 1-4 97.6 2 × 10¹⁶ 150 Al 20 10 911 38 9 PRESENT 1-5 99.8 7 × 10¹⁸ 150 Al 20 10 911 42 5.3 INVENTION 1-6 97.6 2 × 10¹⁵ 8 Al 0.01 10 911 38 9 1-7 97.6 2 × 10¹⁶ 30 Al 0.4 10 911 38 9 1-8 97.6 2 × 10¹⁰ 350 Al 13 10 911 38 9 1-9 97.6 2 × 10¹⁶ 500 Al 50 10 911 38 9 1-10 97.6 2 × 10¹⁶ 750 Al 150 10 911 38 9 1-11 97.6 2 × 10¹⁶ 150 Al 20 500 911 27 11 1-12 97.6 2 × 10¹⁰ 150 Al 20 100 911 34 10 1-13 97.6 2 × 10¹⁶ 150 Al 20 1 911 42 5.2 1-14 97.6 2 × 10¹⁶ 150 Al 20 0.1 911 38 9 1-15 97.6 2 × 10¹⁵ 160 Al 20 0.01 911 31 14 1-16 97.6 2 × 10¹⁶ 150 Al 20 10 911 38 9 1-17 97.6 2 × 10¹⁵ 150 Al 20 10 911 38 9 1-18 97.6 2 × 10¹⁵ 150 Al 20 10 911 38 9 1-19 97.6 2 × 10¹⁰ 150 Al 20 10 911 38 9 1-20 97.6 2 × 10¹⁵ 150 Al 20 10 911 38 9 1-21 97.6 2 × 10¹⁵ 150 Al 20 10 911 38 9 1-22 97.6 2 × 10¹⁵ 150 Al 20 10 911 38 9 1-23 97.6 2 × 10¹⁶ 150 Al 20 10 911 38 9 1-24 97.6 2 × 10¹⁶ 150 Al 20 10 911 38 9 1-25 97.6 2 × 10¹⁶ 150 Al 20 10 911 38 9 1-26 97.6 2 × 10¹⁵ 150 Al 20 10 911 38 9 1-27 97.6 2 × 10¹⁵ 150 Al 20 10 911 38 9 SECOND SAMPLE THIRD SAMPLE ACCUMU- ACCUMU- ACCUMU- ACCUMU- KEEPING LATION LATION COOL- LATION LATION CONDI- TEMPER- KEEPING DEGREE OF DEGREE OF ING DIS- DEGREE OF DEGREE OF TION ATURE TIME [200] PLANE [222] PLANE RATE TANCE [200] PLANE [222] PLANE No. (° C.) (s) (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 1-1 1000 10 13 13 100 75 13 13 EXAMPLE 1-2 900 10 24 12 100 78 24 12 EXAMPLE 1-3 1000 10 38 8 100 78 38 8 OF 1-4 1000 10 48 3.8 100 78 48 3.8 PRESENT 1-5 1000 10 72 0.2 100 78 72 0.2 INVENTION 1-6 1000 10 39 10 100 4 39 10 1-7 1000 10 40 8 100 16 40 8 1-8 1000 10 48 3.8 100 190 48 3.8 1-9 1000 10 48 3.8 100 250 48 3.8 1-10 1000 10 41 11 100 320 30 15 1-11 1000 10 39 8 100 78 39 8 1-12 1000 10 44 4.3 100 78 44 4.3 1-13 1000 10 55 2.1 100 78 55 11 1-14 1000 10 52 2.8 100 78 52 2.8 1-15 1000 10 40 8 100 78 40 8 1-16 1100 10 58 2.2 100 78 58 2.2 1-17 1250 10 63 1.3 100 78 63 1.3 1-18 1350 10 67 0.4 100 78 67 0.4 1-19 1000 0 42 8.5 100 78 42 8.5 1-20 1000 60 55 2.1 100 78 55 2.1 1-21 1000 600 60 1.7 100 78 60 1.7 1-22 1000 3600 63 1.3 100 78 63 1.3 1-23 1000 36000 64 1.2 100 78 64 1.2 1-24 1000 10 48 3.8 1000 78 39 8 1-25 1000 10 48 3.8 10 78 48 3.8 1-26 1000 10 48 3.8 1 78 48 3.8 1-27 1000 10 48 3.8 0.1 78 48 3.8

Further, an alloying ratio of the metal layer and a ratio of an α single phase region in each of the Fe-based metal plates were measured in the following manner. First, in-plane distribution of the Fe content and in-plane distribution of the Al content in the cross section perpendicular to the surface of the Fe-based metal plate were measured by an EPMA (Electron Probe Micro-Analysis) method. At this time, as for a field of view, its dimension in a direction parallel to the surface of the Fe-based metal plate (rolling direction) was set to 1 mm and its dimension in the thickness direction was set to a thickness of the Fe-based metal plate. Then, a region where the Fe content was 0.5 mass % or less and the Al content was 99.5 mass % or more was regarded as an alloy layer, and the alloying ratio was found from the aforesaid expression (3). Further, a region where the Al content was 0.9 mass % or more was regarded as an alloy region, and the ratio of the α single phase region was found from the aforesaid expression (4). Results of these are listed in Table 2.

Further, magnetic flux density B50 and saturation magnetic flux density Bs to a magnetizing force of 5000 A/m were measured. In the measurement of the magnetic flux density B50, a SST (Single Sheet Tester) was used, and a measurement frequency was set to 50 Hz. In the measurement of the saturation magnetic flux density Bs, a VSM (Vibrating Sample Magnetometer) was used and a magnetizing force of 0.8×10⁶ A/m was applied. Then, a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Results of these are listed in Table 2.

TABLE 2 RATIO OF ACCUMULATION ACCUMULATION α SINGLE DEGREE OF DEGREE OF CONDITION ALLOYING PHASE {200} PLANE {222} PLANE B50 Bs No. RATE (%) (%) (%) (%) (T) (T) B50/Bs COMPARATIVE 1-1 — 0 13 13 1.70 2.16 0.79 EXAMPLE 1-2 73 0.9 24 12 1.55 1.95 0.79 EXAMPLE 1-3 87 35 38 8 1.71 1.95 0.88 OF 1-4 87 35 48 3.8 1.74 1.95 0.89 PRESENT 1-5 87 35 72 0.2 1.84 1.95 0.94 INVENTION 1-6 100 100 39 10 1.88 2.14 0.88 1-7 100 81 40 8 1.90 2.14 0.89 1-8 75 23 48 3.8 1.89 2.10 0.90 1-9 60 13 48 3.8 1.78 2.00 0.89 1-10 40 4 41 11 1.61 1.85 0.87 1-11 31 3 39 8 1.72 1.95 0.88 1-12 54 13 44 4.3 1.72 1.95 0.88 1-13 94 47 55 2.1 1.76 1.95 0.90 1-14 100 61 52 2.8 1.75 1.95 0.90 1-15 100 75 40 8 1.73 1.95 0.89 1-16 100 34 58 2.2 1.77 1.95 0.91 1-17 100 64 63 1.3 1.80 1.95 0.92 1-18 100 86 67 0.4 1.82 1.95 0.93 1-19 68 1.1 42 8.5 1.74 1.95 0.89 1-20 95 54 55 2.1 1.75 1.95 0.90 1-21 100 65 60 1.7 1.78 1.95 0.91 1-22 100 85 63 1.3 1.81 1.95 0.93 1-23 100 100 64 1.2 1.80 1.95 0.92 1-24 87 35 48 3.8 1.72 1.95 0.88 1-25 87 35 48 3.8 1.74 1.95 0.89 1-26 87 35 48 3.8 1.74 1.95 0.89 1-27 87 35 48 3.8 1.74 1.95 0.89

As listed in Table 1, in examples of the present invention (conditions No. 1-3 to No. 1-27), the accumulation degree of the {200} planes in the α phase was high at each of the stages of the heat treatment. Further, as listed in Table 2, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were high. As listed in Table 2, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the α phase was not less than 30% nor more than 99% and the accumulation degree of the {222} planes in the α phase was not less than 0.01% nor more than 30% were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.87 or more. That is, according to the examples of the present invention, an excellent magnetic property was obtained.

On the other hand, in the condition No. 1-1 being a comparative example, since the metal layer was not formed, a high accumulation degree of the {200} planes in the α phase was not obtained and a good magnetic property was not obtained even though high-density dislocation existed in the base metal plate. In the condition No. 1-2 being a comparative example, since the heating temperature was lower than the A3 point (911° C.), improvement in the accumulation degree of the {200} planes in the α phase owing to the γ-α transformation was not caused, and a good magnetic property was not obtained.

Second Experiment

In a second experiment, six kinds of base metal plates different in composition were used, and various kinds of materials were used as the metal layers, and correlations between 73 kinds of conditions (condition No. 2-1 to condition No. 2-73) and an accumulation degree of {200} planes and an accumulation degree of {222} planes were studied.

Components contained in six kinds of the base metal plates used in the second experiment are listed in Table 3. The balance of the base metal plates was Fe and inevitable impurities. Table 3 also lists actually measured values of A3 points of the base metal plates. The base metal plates were fabricated in such a manner that an ingot was produced by vacuum melting, followed by hot rolling and cold rolling. In the hot rolling, the ingot with a 230 mm thickness heated to 1000° C. was thinned to a 50 mm thickness, whereby a hot-rolled plate was obtained. Thereafter, plate materials different in thickness were cut out from the hot-rolled plate by machining, and the plate materials were subjected to the cold rolling with rolling reduction ratios listed in Table 4, subjected to shot blasting, or subjected to the both. In the shot blasting, iron beads each with a 1 mm to 3 mm diameter were made to continuously collide with both surfaces of the base metal plates for ten seconds each. Whether the shot blasting was performed or not and the thickness of each of the obtained base metal plates (cold-rolled plates) are listed in Table 4 and Table 5.

TABLE 3 COMPOSITION OF COMPONENT ELEMENT (mass %) A3 POINT BASE METAL PLATE C Si Mn Al P N S O OTHERS (° C.) A 0.0003 0.05 0.15 0.0005 0.0001 0.0002 <0.0004 0.0002 Ti: 0.03 910 B 0.0002 0.1 0.12 0.0002 0.0001 0.0003 <0.0004 0.0001 Zr: 0.02 911 C 0.0002 0.3 0.08 0.05 0.0001 0.0003 <0.0004 0.0001 916 D 0.0001 0.4 0.12 0.15 0.0001 0.0002 <0.0004 0.0001 922 E 0.0001 0.5 1.0 0.21 0.0001 0.0003 <0.0004 0.0001 Cr: 2.0 914 F 0.0001 0.01 1.7 0.01 0.0001 0.0002 <0.0004 0.0001 872

Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope in the same manner as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 50 μm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 4 and Table 5.

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 19% to 27% range and the accumulation degree of the {222} planes in the α phase was within a 18% to 25% range in each of the base metal plates.

Thereafter, metal layers were formed on a front Surface and a rear surface of each of the base metal plates by an IP method, a hot dipping method, a sputtering method, or a vapor deposition method, except in the conditions No. 2-1, No. 2-13, No. 2-25, No. 2-37, No. 2-43, No. 2-49, No. 2-55, No. 2-61, and No. 2-67. Thickness of each of the metal layers (total thickness on the both surfaces) is listed in Table 4 and Table 5. Si layers were formed by the IP method, Sn layers were formed by the hot dipping method, and Ti layers were formed by the sputtering method. Further, Ga layers were formed by the vapor deposition method, Ge layers were formed by the vapor deposition method, No layers were formed by the sputtering method, V layers were formed by the sputtering method, Cr layers were formed by the sputtering method, and As layers were formed by the vapor deposition method.

Subsequently, heat treatment was applied on the base metal plates, on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 4 and Table 5.

TABLE 4 BASE METAL PLATE REDUCTION DISLOCATION METAL LAYER CONDITION COMPO- RATE DENSITY THICKNESS THICKNESS No. SITION BLASTING (%) (m/m³) (μm) ELEMENT (μm) COMPARATIVE 2-1 A WITHOUT 97.2 1 × 10¹⁶ 250 NONE EXAMPLE 2-2 A WITHOUT 97.2 1 × 10¹⁶ 250 Si 33 EXAMPLE 2-3 A WITHOUT 971 1 × 10¹⁶ 250 Si 33 OF 2-4 A WITHOUT 972 1 × 10¹⁶ 250 Si 33 PRESENT 2-5 A WITHOUT 97.2 1 × 10¹⁶ 250 Si 33 INVENTION 2-6 A WITHOUT 97.2 1 × 10¹⁶ 250 Si 33 2-7 B WITH 0 1 × 10¹⁴ 350 Si 38 2-8 B WITH 49 8 × 10¹⁴ 350 Si 38 2-9 B WITH 50 1 × 10¹⁵ 350 Si 38 2-10 B WITH 70 6 × 10¹⁵ 350 Si 38 2-11 B WITH 90 5 × 10¹⁵ 350 Si 38 2-12 B WITH 97 1 × 10¹⁷ 350 Si 38 COMPARATIVE 2-13 C WITHOUT 98.2 3 × 10¹⁶ 326 NONE EXAMPLE 2-14 C WITHOUT 98.2 3 × 10¹⁶ 326 Sn 17 EXAMPLE 2-15 C WITHOUT 98.2 3 × 10¹⁶ 326 Sn 17 OF 2-16 C WITHOUT 98.2 3 × 10¹⁶ 326 Sn 17 PRESENT 2-17 C WITHOUT 98.2 3 × 10¹⁶ 326 Sn 17 INVENTION 2-18 C WITHOUT 98.2 3 × 10¹⁶ 326 Sn 17 2-19 D WITH 0 1 × 10¹⁴ 500 Sn 23 2-20 D WITH 49 7 × 10¹⁴ 500 Sn 23 2-21 D WITH 50 1 × 10¹⁵ 500 Sn 23 2-22 D WITH 70 5 × 10¹⁵ 500 Sn 23 2-23 D WITH 90 7 × 10¹⁶ 500 Sn 23 2-24 D WITH 97 1 × 10¹⁷ 500 Sn 23 COMPARATIVE 2-25 E WITHOUT 97.1 2 × 10¹⁶ 100 NONE EXAMPLE 2-26 E WITHOUT 97.1 2 × 10¹⁶ 100 Ti 8 EXAMPLE 2-27 E WITHOUT 97.1 2 × 10¹⁶ 100 Ti 8 OF 2-28 E WITHOUT 97.1 2 × 10¹⁶ 100 Ti 8 PRESENT 2-29 E WITHOUT 97.1 2 × 10¹⁶ 100 Ti 8 INVENTION 2-30 E WITHOUT 97.1 2 × 10¹⁶ 100 Ti 8 2-31 F WITH 0 1 × 10¹⁴ 700 Ti 29 2-32 F WITH 49 8 × 10¹⁴ 700 Ti 29 2-33 F WITH 50 1 × 10¹⁵ 700 Ti 29 2-34 F WITH 70 7 × 10¹⁵ 700 Ti 29 2-35 F WITH 90 5 × 10¹⁶ 700 Ti 29 2-36 F WITH 97 1 × 10¹⁷ 700 Ti 29 FIRST SAMPLE ACCUMULATION ACCUMULATION SECOND SAMPLE HETING MEASURED DEGREE OF DEGREE OF KEEPING KEEPING CONDITION RATE TEMPERATURE [200] PLANE [222] PLANE TEMPERATURE TIME No. (° C./s) (° C.) (%) (%) (° C.) (s) COMPARATIVE 2-1 20 910 18 14 1000 20 EXAMPLE 2-2 20 900 21 13 900 20 EXAMPLE 2-3 20 910 36 8 1000 20 OF 2-4 20 910 36 8 1100 20 PRESENT 2-5 20 910 35 8 1250 20 INVENTION 2-6 20 910 35 8 1350 20 2-7 10 911 25 13 1200 120 2-8 10 911 26 11 1200 120 2-9 10 911 27 10 1200 120 2-10 10 911 39 7 1200 120 2-11 10 911 41 5.1 1200 120 2-12 10 911 48 4.2 1200 120 COMPARATIVE 2-13 8 916 19 12 1000 40 EXAMPLE 2-14 8 900 24 12 900 40 EXAMPLE 2-15 8 916 45 5.7 1000 40 OF 2-16 8 916 45 5.7 1100 40 PRESENT 2-17 8 916 45 5.7 1250 40 INVENTION 2-18 8 916 45 5.7 1350 40 2-19 1 922 25 13 1050 1800 2-20 1 922 26 11 1050 1800 2-21 1 922 27 10 1050 1800 2-22 1 922 37 8 1050 1800 2-23 1 922 42 5.2 1050 1800 2-24 1 922 46 5.6 1050 1800 COMPARATIVE 2-25 10 914 19 12 1000 40 EXAMPLE 2-26 10 900 23 12 900 40 EXAMPLE 2-27 10 914 45 5.7 1000 40 OF 2-28 10 914 45 5.7 1100 40 PRESENT 2-29 10 914 45 5.7 1250 40 INVENTION 2-30 10 914 45 5.7 1350 40 2-31 0.1 872 25 12 950 350 2-32 0.1 872 25 11 950 360 2-33 0.1 872 27 10 950 360 2-34 0.1 872 38 7 950 380 2-35 0.1 872 41 8 950 360 2-36 0.1 872 43 5.3 950 360 SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION COOL- ACCUMULATION ACCUMULATION DEGREE OF DEGREE OF ING DIS- DEGREE OF DEGREE OF CONDITION [200] PLANE [222] PLANE RATE TANCE [200] PLANE [222] PLANE No. (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 2-1 13 13 200 125 13 13 EXAMPLE 2-2 23 11 200 132 23 11 EXAMPLE 2-3 49 3.9 200 132 49 3.9 OF 2-4 60 1.9 200 132 60 1.9 PRESENT 2-5 75 0.5 200 132 75 0.5 INVENTION 2-6 74 0.6 200 132 74 0.6 2-7 30 12 80 185 30 12 2-8 31 10 80 185 31 10 2-9 41 5.8 80 185 41 5.8 2-10 72 0.9 80 185 72 0.9 2-11 75 0.8 80 185 75 0.8 2-12 92 0.1 80 185 92 0.1 COMPARATIVE 2-13 13 13 50 163 13 13 EXAMPLE 2-14 25 12 50 175 25 12 EXAMPLE 2-15 53 2.5 50 175 53 2.5 OF 2-16 73 0.6 50 175 73 0.6 PRESENT 2-17 95 0.1 50 175 95 0.1 INVENTION 2-18 74 0.8 50 175 74 0.8 2-19 30 10 100 265 30 10 2-20 35 9 100 265 35 9 2-21 43 5.4 100 265 43 5.4 2-22 69 1.5 100 265 69 1.5 2-23 73 0.8 100 265 73 0.8 2-24 77 0.5 100 265 77 0.6 COMPARATIVE 2-25 13 13 10 50 13 13 EXAMPLE 2-26 25 12 10 54 25 12 EXAMPLE 2-27 53 2.5 10 54 53 2.5 OF 2-28 73 0.6 10 54 73 0.6 PRESENT 2-29 95 0.1 10 54 95 0.1 INVENTION 2-30 74 0.8 10 54 74 0.8 2-31 31 9 80 280 30 9 2-32 32 10 80 280 30 12 2-33 41 6 80 280 36 9 2-34 52 2.8 80 280 46 6 2-35 58 2.1 80 280 50 2.9 2-36 63 1.6 80 280 54 2.9

TABLE 5 BASE METAL PLATE REDUCTION DISLOCATION METAL LAYER CONDITION COMPO- RATE DENSITY THICKNESS THICKNESS No. SITION BLASTING (%) (m/m³) (μm) ELEMENT (μm) COMPARATIVE 2-37 A WITH 70 8 × 10¹⁵ 350 NONE EXAMPLE 2-38 A WITH 70 8 × 10¹⁵ 350 Ga 18 EXAMPLE 2-39 A WITH 70 8 × 10¹⁵ 350 Ga 18 OF 2-40 A WITH 70 8 × 10¹⁵ 350 Ga 18 PRESENT 2-41 A WITH 70 8 × 10¹⁵ 350 Ga 18 INVENTION 2-42 A WITH 70 8 × 10¹⁵ 350 Ga 18 COMPARATIVE 2-43 B WITH 78 7 × 10¹⁸ 240 NONE EXAMPLE 2-44 B WITH 78 7 × 10¹⁸ 240 Ge 11 EXAMPLE 2-45 B WITH 78 7 × 10¹⁸ 240 Ge 11 OF 2-46 B WITH 78 7 × 10¹⁸ 240 Ge 11 PRESENT 2-47 B WITH 78 7 × 10¹⁸ 240 Ge 11 INVENTION 2-48 B WITH 78 7 × 10¹⁸ 240 Ge 11 COMPARATIVE 2-49 C WITH 50 1 × 10¹⁷ 500 NONE EXAMPLE 2-50 C WITH 50 1 × 10¹⁷ 500 Mo 8 EXAMPLE 2-51 C WITH 50 1 × 10¹⁷ 500 Mo 8 OF 2-52 C WITH 50 1 × 10¹⁷ 500 Mo 8 PRESENT 2-53 C WITH 50 1 × 10¹⁷ 500 Mo 8 INVENTION 2-54 C WITH 50 1 × 10¹⁷ 500 Mo 8 COMPARATIVE 2-55 D WITH 90 3 × 10¹⁶ 150 NONE EXAMPLE 2-56 D WITH 90 3 × 10¹⁶ 150 V 6 EXAMPLE 2-57 D WITH 90 3 × 10¹⁶ 150 V 6 OF 2-58 D WITH 90 3 × 10¹⁶ 150 V 6 PRESENT 2-59 D WITH 90 3 × 10¹⁶ 150 V 6 INVENTION 2-60 D WITH 90 3 × 10¹⁶ 150 V 6 COMPARATIVE 2-61 E WITH 95 6 × 10¹⁶ 100 NONE EXAMPLE 2-62 E WITH 95 6 × 10¹⁶ 100 Cr 5 EXAMPLE 2-63 E WITH 95 6 × 10¹⁶ 100 Cr 5 OF 2-64 E WITH 95 6 × 10¹⁶ 100 Cr 5 PRESENT 2-65 E WITH 95 6 × 10¹⁶ 100 Cr 5 INVENTION 2-66 E WITH 95 6 × 10¹⁶ 100 Cr 5 COMPARATIVE 2-67 F WITH 80 2 × 10¹⁵ 200 NONE EXAMPLE 2-68 F WITH 80 2 × 10¹⁵ 200 As 11 EXAMPLE 2-69 F WITH 80 2 × 10¹⁵ 200 As 11 OF 2-70 F WITH 80 2 × 10¹⁵ 200 As 11 PRESENT 2-71 F WITH 80 2 × 10¹⁵ 200 AS 11 INVENTION 2-72 F WITH 80 2 × 10¹⁵ 200 As 11 2-73 F WITH 80 2 × 10¹⁵ 200 As 11 FIRST SAMPLE ACCUMULATION ACCUMULATION SECOND SAMPLE HETING MEASURED DEGREE OF DEGREE OF KEEPING KEEPING CONDITION RATE TEMPERATURE {200} PLANE {222} PLANE TEMPERATURE TIME No. (° C./s) (° C.) (%) (%) (° C.) (s) COMPARATIVE 2-37 50 910 19 13 1000 120 EXAMPLE 2-38 50 900 21 13 900 120 EXAMPLE 2-39 50 910 34 8 1000 120 OF 2-40 50 910 34 8 1100 120 PRESENT 2-41 50 910 34 8 1250 120 INVENTION 2-42 50 910 34 8 1350 120 COMPARATIVE 2-43 30 911 19 13 1000 25 EXAMPLE 2-44 30 900 23 11 900 25 EXAMPLE 2-45 30 911 41 6.3 1000 25 OF 2-46 30 911 41 6.3 1100 25 PRESENT 2-47 30 911 41 6.3 1250 25 INVENTION 2-48 30 911 41 6.3 1350 25 COMPARATIVE 2-49 10 916 18 15 1000 360 EXAMPLE 2-50 10 900 24 12 900 360 EXAMPLE 2-51 10 916 45 5.2 1000 360 OF 2-52 10 916 45 5.2 1100 360 PRESENT 2-53 10 916 45 5.2 1250 350 INVENTION 2-54 10 916 45 5.2 1350 350 COMPARATIVE 2-55 1 922 17 14 1000 1800 EXAMPLE 2-56 1 900 23 11 900 1800 EXAMPLE 2-57 1 922 42 6.2 1000 1800 OF 2-58 1 922 42 6.2 1100 1800 PRESENT 2-59 1 922 42 6.2 1250 1800 INVENTION 2-60 1 922 42 6.2 1350 1800 COMPARATIVE 2-61 5 914 16 14 1000 720 EXAMPLE 2-62 5 900 23 11 900 720 EXAMPLE 2-63 5 914 48 5.6 1000 720 OF 2-64 5 914 48 5.6 1100 720 PRESENT 2-65 5 914 48 5.6 1250 720 INVENTION 2-66 5 814 48 5.6 1350 720 COMPARATIVE 2-67 0.1 872 14 12 950 30 EXAMPLE 2-68 0.1 850 22 13 850 30 EXAMPLE 2-69 0.1 872 32 9.4 950 30 OF 2-70 0.1 872 32 9.4 1050 30 PRESENT 2-71 0.1 872 32 9.4 1150 30 INVENTION 2-72 0.1 872 32 9.4 1250 30 2-73 0.1 872 32 9.4 1350 30 SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION COOL- ACCUMULATION ACCUMULATION DEGREE OF DEGREE OF ING DIS- DEGREE OF DEGREE OF CONDITION {200} PLANE {222} PLANE RATE TANCE {200} PLANE {222} PLANE No. (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 2-37 13 13 50 175 13 13 EXAMPLE 2-38 22 12 50 176 22 12 EXAMPLE 2-39 45 4.8 50 176 45 4.8 OF 2-40 52 2.8 50 176 52 2.8 PRESENT 2-41 68 1.9 50 176 68 1.9 INVENTION 2-42 65 2.1 50 176 65 0.6 COMPARATIVE 2-43 13 13 100 120 13 13 EXAMPLE 2-44 23 11 100 125 23 11 EXAMPLE 2-45 51 2.9 100 125 51 2.9 OF 2-46 63 2.2 100 125 63 2.2 PRESENT 2-47 78 0.8 100 125 78 0.8 INVENTION 2-48 69 1.8 100 125 69 1.8 COMPARATIVE 2-49 13 13 150 250 13 13 EXAMPLE 2-50 25 11 150 251 25 11 EXAMPLE 2-51 55 2.4 150 251 55 2.4 OF 2-52 68 1.8 150 251 68 1.8 PRESENT 2-53 84 0.6 150 251 84 0.6 INVENTION 2-54 73 1.4 150 251 73 1.4 COMPARATIVE 2-55 13 13 80 75 13 13 EXAMPLE 2-56 26 10 80 75 26 10 EXAMPLE 2-57 51 2.7 80 75 51 2.7 OF 2-58 59 2.3 80 75 50 2.3 PRESENT 2-59 71 1.2 80 75 71 1.2 INVENTION 2-60 60 2.4 80 75 00 2.4 COMPARATIVE 2-61 13 13 10 50 13 13 EXAMPLE 2-62 25 10 10 53 25 10 EXAMPLE 2-63 59 2.2 10 53 59 2.2 OF 2-64 65 1.6 10 53 65 1.0 PRESENT 2-65 78 0.9 10 53 78 0.9 INVENTION 2-66 70 1.6 10 53 70 1.6 COMPARATIVE 2-67 13 13 1 100 13 13 EXAMPLE 2-68 23 11 1 101 23 11 EXAMPLE 2-69 39 8.4 1 101 39 8.4 OF 2-70 44 5.4 1 101 44 5.4 PRESENT 2-71 56 2.6 1 101 56 2.6 INVENTION 2-72 73 1.5 1 101 73 1.5 2-73 70 1.6 1 101 70 1.6

Further, an alloying ratio of the metal layer and a ratio of an α single phase region in each Fe-based metal plate were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass % or less and the content of ferrite former was 99.5% or more was regarded as an alloy layer. Further, in finding the ratio of the α single phase region, an alloy region was decided as described in the following. In the conditions No. 2-2 to No. 2-12 using Si as the metal layers, a region where the Si content was 1.9 mass % or more was regarded as the alloy region. In the conditions No. 2-14 to No. 2-24 using Sn as the metal layers, a region where the Sn content was 3.0 mass % or more was regarded as the alloy region. In the conditions No. 2-26 to No. 2-36 using Ti as the metal layers, a region where the Ti content was 1.2 mass % or more was regarded as the alloy region. In the conditions No. 2-38 to No. 2-42 using Ga as the metal layers, a region where the Ga content was 4.1 mass % or more was regarded as the alloy region. In the conditions No. 2-44 to No. 2-48 using Ge as the metal layers, a region where the Ge content was 6.4 mass % or more was regarded as the alloy region. In the conditions No. 2-50 to No. 2-54 using Mo as the metal layers, a region where the Mo content was 3.8 mass % or more was regarded as the alloy region. In the conditions No. 2-56 to No. 2-60 using V as the metal layers, a region where the V content was 1.8 mass % or more was regarded as the alloy region. In the conditions No. 2-62 to No. 2-66 using Cr as the metal layers, a region where the Cr content was 13.0 mass % or more was regarded as the alloy region. In the conditions No. 2-68 to No. 2-73 using As as the metal layers, a region where the As content was 3.4 mass % or more was regarded as the alloy region. Results of these are listed in Table 6 and Table 7.

Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Results of these are listed in Table 6 and Table 7.

TABLE 6 RATIO OF ACCUMULATION ACCUMULATION ALLOYING α SINGLE DEGREE OF DEGREE OF CONDITION RATE PHASE {200} PLANE {222} PLANE B50 Bs No. (%) (%) (%) (%) (T) (T) B50/Bs COMPARATIVE 2-1 — 0 13 13 1.70 2.16 0.79 EXAMPLE 2-2  69 0.9 23 11 1.55 1.96 0.79 EXAMPLE 2-3 100 8.4 49 3.9 1.75 1.96 0.89 OF 2-4 100 16 60 1.9 1.77 1.96 0.90 PRESENT 2-5 100 36 75 0.5 1.83 1.96 0.93 INVENTION 2-8 100 47 74 0.6 1.82 1.96 0.93 2-7 100 38 30 12 1.71 1.99 0.86 2-8 100 38 31 10 1.73 1.99 0.87 2-9 100 37 41 5.8 1.77 1.99 0.89 2-10 100 38 72 0.9 1.83 1.99 0.92 2-11 100 37 75 0.8 1.85 1.99 0.93 2-12 100 38 92 0.1 1.91 1.99 0.96 COMPARATIVE 2-13 — 0 13 13 1.67 2.16 0.77 EXAMPLE 2-14  75 0.4 25 12 1.53 1.94 0.79 EXAMPLE 2-15 100 4.7 53 2.5 1.75 1.94 0.90 OF 2-16 100 11 73 0.6 1.77 1.94 0.91 PRESENT 2-17 100 26 95 0.1 1.90 1.94 0.98 INVENTION 2-18 100 31 74 0.8 1.77 1.94 0.91 2-19 100 19 30 10 1.69 1.96 0.86 2-20 100 19 35 9 1.71 1.96 0.87 2-21 100 18 43 5.4 1.74 1.96 0.89 2-22 100 20 69 1.5 1.78 1.96 0.91 2-23 100 20 73 0.8 1.80 1.96 0.92 2-24 100 19 77 0.6 1.82 1.96 0.93 COMPARATIVE 2-25 — 0 13 13 1.68 2.16 0.78 EXAMPLE 2-26  75 0.4 25 12 1.55 1.96 0.79 EXAMPLE 2-27 100 4.7 53 2.5 1.76 1.96 0.90 OF 2-28 100 11 73 0.6 1.81 1.96 0.92 PRESENT 2-29 100 26 97 0.1 1.91 1.96 0.97 INVENTION 2-30 100 31 74 0.8 1.82 1.96 0.93 2-31 100 19 31 9 1.74 2.05 0.85 2-32 100 19 32 10 1.76 2.05 0.86 2-33 100 18 41 6 1.80 2.05 0.88 2-34 100 20 52 2.8 1.85 2.05 0.90 2-35 100 20 58 2.1 1.87 2.05 0.91 2-36 100 19 63 1.6 1.89 2.05 0.92

TABLE 7 ACCUMULATION ACCUMULATION RATIO OF DEGREE OF DEGREE OF CONDITION ALLOYING α SINGLE {200} PLANE {222} PLANE B50 Bs No. RATE (%) PHASE (%) (%) (%) (T) (T) B50/Bs COMPARATIVE 2-37 — 0 13 13 1.70 2.16 0.79 EXAMPLE 2-38  87 0.8 22 12 1.56 1.98 0.79 EXAMPLE 2-39 100 3.6 45 4.8 1.76 1.98 0.89 OF 2-40 100 8.9 52 2.8 1.78 1.98 0.90 PRESENT 2-41 100 19.5 68 1.9 1.84 1.98 0.93 INVENTION 2-42 100 27.3 65 0.6 1.84 1.98 0.93 COMPARATIVE 2-43 — 0 13 13 1.70 2.16 0.79 EXAMPLE 2-44  68 0.9 22 12 1.59 2.01 0.79 EXAMPLE 2-45  95 7.5 51 2.9 1.79 2.01 0.89 OF 2-46 100 18.4 63 2.2 1.81 2.01 0.90 PRESENT 2-47 100 31 78 0.8 1.87 2.01 0.93 INVENTION 2-48 100 44 69 1.8 1.87 2.01 0.93 COMPARATIVE 2-49 — 0 13 13 1.68 2.16 0.78 EXAMPLE 2-50  47 0.3 25 11 1.63 2.06 0.79 EXAMPLE 2-51  98 2.8 55 2.4 1.85 2.06 0.90 OF 2-52 100 5.9 68 1.8 1.88 2.06 0.91 PRESENT 2-53 100 8.4 84 0.6 1.92 2.06 0.93 INVENTION 2-54 100 11.8 73 1.4 1.89 2.06 0.92 COMPARATIVE 2-55 — 0 13 13 1.68 2.16 0.78 EXAMPLE 2-56  78 0.8 26 10 1.63 2.01 0.81 EXAMPLE 2-57 100 3.5 51 2.7 1.81 2.01 0.90 OF 2-58 100 6.9 59 2.3 1.83 2.01 0.91 PRESENT 2-59 100 9.5 71 1.2 1.84 2.01 0.92 INVENTION 2-60 100 12.1 60 2.4 1.83 2.01 0.91 COMPARATIVE 2-61 — 0 13 13 1.68 2.16 0.78 EXAMPLE 2-62  37 0.9 25 10 1.53 1.98 0.78 EXAMPLE 2-63 100 8.6 59 2.2 1.76 1.96 0.90 OF 2-64 100 14.2 65 1.6 1.79 1.96 0.91 PRESENT 2-65 100 25.7 78 0.9 1.82 1.96 0.93 INVENTION 2-66 100 32.8 70 1.6 1.80 1.96 0.92 COMPARATIVE 2-67 — 0 13 13 1.67 2.16 0.77 EXAMPLE 2-68  45 0.8 23 11 1.54 1.98 0.78 EXAMPLE 2-69  88 6.7 39 8.4 1.72 1.98 0.87 OF 2-70 100 13.8 44 5.4 1.74 1.98 0.88 PRESENT 2-71 100 28.4 56 2.6 1.80 1.98 0.91 INVENTION 2-72 100 39.3 73 1.5 1.83 1.98 0.92 2-73 100 47.5 70 1.6 1.79 1.98 0.90

As listed in Table 4 and Table 5, in examples of the present invention (conditions No. 2-3 to No. 2-12, No. 2-15 to No. 2-24, No. 2-27 to No. 2-36, No. 2-39 to No. 2-42, No. 2-45 to No. 2-48, No. 2-51 to No. 2-54, No. 2-57 to No. 2-60, No. 2-63 to No. 2-66, and No. 2-69 to No. 2-73), the accumulation degree of the {200} planes in the α phase was high at each of the stages of the heat treatment. Further, as listed in Table 6 and Table 7, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were high. As listed in Table 6 and Table 7, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the α phase was not less than 30% nor more than 99% and the accumulation degree of the {222} planes in the α phase was not less than 0.01% nor more than 30% were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more. That is, according to the examples of the present invention, an excellent magnetic property was obtained.

On the other hand, in the conditions No. 2-1, No. 2-13, No. 2-25, No. 2-37, No. 2-43, No. 2-49, No. 2-55, No. 2-61, and No. 2-67 being comparative examples, since the metal layer was not formed, a high accumulation degree of the {200} planes in the α phase was not obtained and a good magnetic property was not obtained even though high-density dislocation existed in the base metal plate. In the conditions No. 2-2, No. 2-14, No. 2-26, No. 2-38, No. 2-44, No. 2-50, No. 2-56, No. 2-62, and No. 2-68 being comparative examples, since the heating temperature was lower than the A3 point, improvement in the accumulation degree of the {200} planes in the α phase owing to the γ-α transformation was not caused, and a good magnetic property was not obtained.

Third Experiment

In a third experiment, six kinds of base metal plates different in composition were used, and various kinds of materials were used as the metal layers, and correlations between 42 kinds of conditions (condition No. 3-1 to condition No. 3-42) and an accumulation degree of {200} planes and an accumulation degree of {222} planes were studied.

Components contained in six kinds of the base metal plates used in the third experiment are listed in Table 8. The balance of the base metal plates was Fe and inevitable impurities. Table 8 also lists actually measured values of A3 points of the base metal plates. The base metal plates were fabricated in such a manner that an ingot was produced by vacuum melting, followed by hot rolling and cold rolling. In the hot rolling, the ingot with a 230 mm thickness heated to 1000° C. was thinned to a 50 mm thickness, whereby a hot-rolled plate was obtained. Thereafter, plate materials different in thickness were cut out from the hot-rolled plate by machining, and the plate materials were subjected to the cold rolling with rolling reduction ratios listed in Table 9, and a shear strain was generated. To generate the shear strain, upper and lower reduction rolls are rotated at different speeds at the time of the cold rolling. Some of the base metal plates were also subjected to shot blasting as in the second embodiment. Whether the shot blasting was performed or not, the shear strain, and the thickness of each of the obtained base metal plates (cold-rolled plates) are listed in Table 9. Note that the shear strain was calculated from diameters of the reduction rolls and a difference in speed between the reduction rolls.

TABLE 8 COMPOSITION OF COMPONENT ELEMENT (mass %) A3 POINT BASE METAL PLATE C Si Mn Al P N S O OTHERS (° C.) G 0.001 0.14 0.23 0.001 0.0001 0.0002 <0.0004 0.0002 Cu: 0.01 898 H 0.0002 0.08 0.06 0.0015 0.0021 0.0004 <0.0004 0.0003 Ni: 0.15 887 I 0.03 0.09 0.09 0.0008 0.0025 0.0003 <0.0004 0.0007 Cu: 0.15 905 J 0.0001 0.07 0.12 0.15 0.0004 0.0002 <0.0004 0.0005 Ni: 0.5 868 K 0.0003 0.85 0.07 0.53 0.0003 0.0003 <0.0004 0.0001 921 L 0.0002 0.03 0.08 0.7 0.0003 0.0002 <0.0004 0.0001 925

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 19% to 27% range and the accumulation degree of the {222}planes in the α phase was within a 18% to 25% range in each of the base metal plates.

Thereafter, metal layers were formed on a front surface and a rear surface of each of the base metal plates by an IP method, a hot dipping method, a sputtering method, or a rolling clad method, except in the conditions No. 3-13, No. 3-19, No. 3-25, No. 3-31, and No. 3-37. Thickness of each of the metal layers (total thickness on the both surfaces) is listed in Table 9. Al layers with a 0.7 μm thickness were formed by the IP method, Al layers with a 7 μm to 68 μm thickness were formed by the hot dipping method, and Al layers with a 205 μm or 410 μm thickness were formed by the rolling clad method. Sb layers and W layers were formed by the sputtering method, and Zn layers, Al—Si alloy layers, and Sn—Zn alloy layers were formed by the hot dipping method.

Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 9.

TABLE 9 BASE METAL PLATE REDUCTION METAL LAYER CONDITION COMPO- RATE SHEAR THICKNESS THICKNESS No. SITION BLASTING (%) STRAIN (μm) ELEMENT (μm) COMPARATIVE 3-1 G WITHOUT 70 0 350 Al 24 EXAMPLE 3-2 G WITHOUT 70 0.1 350 Al 24 EXAMPLE 3-3 G WITHOUT 70 0.2 350 Al 24 OF 3-4 G WITHOUT 70 0.4 350 Al 24 PRESENT 3-5 G WITHOUT 70 0.6 350 Al 24 INVENTION 3-6 G WITHOUT 70 0.8 350 Al 24 3-7 G WITH 55 0.4 10 Al 0.7 3-8 G WITH 55 0.4 100 Al 7 3-9 G WITH 55 0.4 500 Al 34 3-10 G WITH 55 0.4 1000 Al 68 3-11 G WITH 55 0.4 3000 Al 205 3-12 G WITH 55 0.4 6000 Al 410 COMPARATIVE 3-13 H WITHOUT 75 0.5 200 NONE EXAMPLE 3-14 H WITHOUT 75 0.5 200 Sb 6 EXAMPLE 3-15 H WITHOUT 75 0.5 200 Sb 6 OF 3-16 H WITHOUT 75 0.5 200 Sb 6 PRESENT 3-17 H WITHOUT 75 0.5 200 Sb 6 INVENTION 3-18 H WITHOUT 75 0.5 200 Sb 6 COMPARATIVE 3-19 I WITHOUT 85 0.6 150 NONE EXAMPLE 3-20 I WITHOUT 85 0.6 150 W 2 EXAMPLE 3-21 I WITHOUT 85 0.6 150 W 2 OF 3-22 I WITHOUT 85 0.6 150 W 2 PRESENT 3-23 I WITHOUT 85 0.6 150 W 2 INVENTION 3-24 I WITHOUT 85 0.6 150 W 2 COMPARATIVE 3-25 J WITH 70 0.2 700 NONE EXAMPLE 3-26 J WITH 70 0.2 700 Zn 44 EXAMPLE 3-27 J WITH 70 0.2 700 Zn 44 OF 3-28 J WITH 70 0.2 700 Zn 44 PRESENT 3-29 J WITH 70 0.2 700 Zn 44 INVENTION 3-30 J WITH 70 0.2 700 Zn 44 COMPARATIVE 3-31 K WITH 65 0.1 300 NONE EXAMPLE 3-32 K WITH 65 0.1 300 90%Al + 10%Si 40 EXAMPLE 3-33 K WITH 65 0.1 300 90%Al + 10%Si 40 OF 3-34 K WITH 65 0.1 300 90%Al + 10%Si 40 PRESENT 3-35 K WITH 65 0.1 300 90%Al + 10%Si 40 INVENTION 3-36 K WITH 65 0.1 300 90%Al + 10%Si 40 COMPARATIVE 3-37 L WITH 60 0.2 500 NONE EXAMPLE 3-38 L WITH 60 0.2 500 92%Sn + 8%Zn 26 EXAMPLE 3-39 L WITH 60 0.2 500 92%Sn + 8%Zn 26 OF 3-40 L WITH 60 0.2 500 92%Sn + 8%Zn 26 PRESENT 3-41 L WITH 60 0.2 500 92%Sn + 8%Zn 26 INVENTION 3-42 L WITH 60 0.2 500 92%Sn + 8%Zn 26 FIRST SAMPLE ACCUMULATION ACCUMULATION SECOND SAMPLE HETING MEASURED DEGREE OF DEGREE OF KEEPING KEEPING CONDITION RATE TEMPERATURE {200} PLANE {222} PLANE TEMPERATURE TIME No. (° C./s) (° C.) (%) (%) (° C.) (s) COMPARATIVE 3-1 1 898 16 14 980 3600 EXAMPLE 3-2 1 898 22 10 980 3600 EXAMPLE 3-3 1 898 27 9 980 3600 OF 3-4 1 898 39 7.5 980 3600 PRESENT 3-5 1 898 42 6.4 980 3600 INVENTION 3-6 1 898 44 5.9 980 3600 3-7 0.01 898 34 7.7 1000 7200 3-8 0.01 898 39 7.6 1000 7200 3-9 0.01 898 41 6.3 1000 7200 3-10 0.01 898 42 5.9 1000 7200 3-11 0.01 898 42 5.6 1000 7200 3-12 0.01 898 41 5.7 1000 7200 COMPARATIVE 3-13 0.1 887 18 15 950 600 EXAMPLE 3-14 0.1 850 23 11 850 600 EXAMPLE 3-15 0.1 887 39 7.8 950 600 OF 3-16 0.1 887 39 7.8 1050 600 PRESENT 3-17 0.1 887 39 7.8 1150 600 INVENTION 3-18 0.1 887 39 7.8 1250 600 COMPARATIVE 3-19 0.2 905 17 13 1000 60 EXAMPLE 3-20 0.2 880 24 10 880 60 EXAMPLE 3-21 0.2 905 44 6.2 1000 60 OF 3-22 0.2 905 44 6.2 1100 60 PRESENT 3-23 0.2 905 44 6.2 1250 60 INVENTION 3-24 0.2 905 44 6.2 1350 60 COMPARATIVE 3-25 2 868 18 12 900 10 EXAMPLE 3-26 2 850 22 12 850 10 EXAMPLE 3-27 2 868 36 8.2 900 10 OF 3-28 2 868 36 8.2 1000 10 PRESENT 3-29 2 868 36 8.2 1100 10 INVENTION 3-30 2 868 36 8.2 1200 10 COMPARATIVE 3-31 0.1 921 14 12 1000 100 EXAMPLE 3-32 0.1 900 23 13 900 100 EXAMPLE 3-33 0.1 921 38 7.3 1000 100 OF 3-34 0.1 921 38 7.3 1100 100 PRESENT 3-35 0.1 921 38 7.3 1200 100 INVENTION 3-36 0.1 921 38 7.3 1300 100 COMPARATIVE 3-37 1 925 15 11 1000 0 EXAMPLE 3-38 1 900 24 12 900 0 EXAMPLE 3-39 1 925 41 7.1 1000 0 OF 3-40 1 925 41 7.1 1100 0 PRESENT 3-41 1 925 41 7.1 1200 0 INVENTION 3-42 1 925 41 7.1 1300 0 SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION COOL- ACCUMULATION ACCUMULATION DEGREE OF DEGREE OF ING DIS- DEGREE OF DEGREE OF CONDITION {200} PLANE {222} PLANE RATE TANCE {200} PLANE {222} PLANE No. (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 3-1 13 13 50 183 13 13 EXAMPLE 3-2 23 10 50 183 23 10 EXAMPLE 3-3 36 6.8 50 183 36 6.8 OF 3-4 52 2.7 50 183 52 2.7 PRESENT 3-5 68 1.9 50 183 68 1.9 INVENTION 3-6 70 1.5 50 183 70 1.5 3-7 42 6.7 1 5 42 6.7 3-8 50 3.1 1 53 50 3.1 3-9 53 2.6 1 265 53 2.6 3-10 55 2.1 1 350 52 3.4 3-11 56 1.9 1 420 45 6.1 3-12 54 2.3 1 450 35 7.6 COMPARATIVE 3-13 13 13 0.1 100 13 13 EXAMPLE 3-14 26 10 0.1 100 26 10 EXAMPLE 3-15 47 5.3 0.1 100 47 5.3 OF 3-16 51 3.3 0.1 100 51 3.3 PRESENT 3-17 64 2.3 0.1 100 64 2.3 INVENTION 3-18 73 1.1 0.1 100 73 1.1 COMPARATIVE 3-19 13 13 5 75 13 13 EXAMPLE 3-20 27 9 5 76 27 9 EXAMPLE 3-21 54 2.6 5 76 54 2.6 OF 3-22 68 2.1 5 76 68 2.1 PRESENT 3-23 78 0.8 5 76 78 0.8 INVENTION 3-24 67 2.3 5 76 67 2.3 COMPARATIVE 3-25 13 13 0.5 300 13 13 EXAMPLE 3-26 24 10 0.5 300 24 10 EXAMPLE 3-27 41 6.8 0.5 300 41 6.8 OF 3-28 49 5.4 0.5 300 49 5.4 PRESENT 3-29 54 3.1 0.5 300 54 3.1 INVENTION 3-30 58 2.7 0.5 300 58 2.7 COMPARATIVE 3-31 13 13 10 150 13 13 EXAMPLE 3-32 25 10 10 160 25 10 EXAMPLE 3-33 47 5.9 10 160 47 5.9 OF 3-34 59 2.8 10 160 59 2.8 PRESENT 3-35 71 1.5 10 160 71 1.5 INVENTION 3-36 63 2.5 10 160 63 2.5 COMPARATIVE 3-37 13 13 500 250 13 13 EXAMPLE 3-38 25 11 500 270 25 11 EXAMPLE 3-39 43 6.3 500 270 43 6.3 OF 3-40 52 3.2 500 270 52 3.2 PRESENT 3-41 52 2.8 500 270 62 2.8 INVENTION 3-42 58 3 500 270 58 3

Further, an alloying ratio of the metal layer and a ratio of an α single phase region in each Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass % or less and the content of ferrite former was 99.5% or more was regarded as an alloy layer. Further, in finding the ratio of the α single phase region, the alloy region was decided as described in the following. In the conditions No. 3-1 to No. 3-12 using Al as the metal layers, a region where the Al content was 0.9 mass % or more was regarded as the alloy region. In the conditions No. 3-14 to No. 3-18 using Sb as the metal layers, a region where the Sb content was 3.6 mass % or more was regarded as the alloy region. In the conditions No. 3-20 to No. 3-24 using W as the metal layers, a region where the W content was 6.6 mass % or more was regarded as the alloy region. In the conditions No. 3-26 to No. 3-30 using Zn as the metal layers, a region where the Zn content was 7.2 mass % or more was regarded as the alloy region. In the conditions No. 3-32 to No. 3-36 using an Al—Si alloy as the metal layers, a region where the Al content was 0.9 mass % or more and the Si content was 0.2 mass % or more was regarded as the alloy region. In the conditions No. 3-38 to No. 3-42 using a Sn—Zn alloy as the metal layers, a region where the Sn content was 2.9 mass % or more and the Zn content was 0.6 mass % or more was regarded as the alloy region. Results of these are listed in Table 10.

Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Results of these are listed in Table 10.

TABLE 10 RATIO OF ACCUMULATION ACCUMULATION ALLOYING α SINGLE DEGREE OF DEGREE OF CONDITION RATE PHASE {200} PLANE {222} PLANE B50 Bs No. (%) (%) (%) (%) (T) (T) B50/Bs COMPARATIVE 3-1 13 13 13 13 1.70 2.16 0.79 EXAMPLE 3-2 23 10 23 10 1.62 2.05 0.79 EXAMPLE 3-3 36 6.8 36 6.8 1.82 2.05 0.89 OF 3-4 52 2.7 52 2.7 1.85 2.05 0.90 PRESENT 3-5 68 1.9 68 1.9 1.89 2.05 0.92 INVENTION 3-6 70 1.5 70 1.5 1.91 2.05 0.93 3-7 100 100 42 6.7 1.80 2.05 0.88 3-8 100 100 50 3.1 1.85 2.05 0.90 3-9 100 25 53 2.6 1.87 2.05 0.91 3-10 100 10.8 55 2.1 1.87 2.05 0.91 3-11 95 3.8 56 1.9 1.85 2.05 0.90 3-12 75 2.1 54 2.3 1.80 2.05 0.88 COMPARATIVE 3-13 — 0 13 13 1.65 2.16 0.76 EXAMPLE 3-14 76 0.2 26 10 1.62 2.04 0.79 EXAMPLE 3-15 100 1.7 47 5.3 1.81 2.04 0.89 OF 3-16 100 3.8 51 3.3 1.84 2.04 0.90 PRESENT 3-17 100 7.5 64 2.3 1.86 2.04 0.91 INVENTION 3-18 100 8.4 73 1.1 1.88 2.04 0.92 COMPARATIVE 3-19 — 0 13 13 1.67 2.16 0.77 EXAMPLE 3-20 57 0.4 27 9 1.58 2.02 0.78 EXAMPLE 3-21 86 2.6 54 2.6 1.81 2.02 0.90 OF 3-22 100 6.8 68 2.1 1.83 2.02 0.91 PRESENT 3-23 100 10.1 78 0.8 1.87 2.02 0.93 INVENTION 3-24 100 13.9 67 2.3 1.84 2.02 0.91 COMPARATIVE 3-25 — 0 13 13 1.67 2.16 0.77 EXAMPLE 3-26 24 0.6 24 10 1.46 1.90 0.77 EXAMPLE 3-27 64 2.7 41 6.8 1.65 1.90 0.87 OF 3-28 89 5.8 49 5.4 1.67 1.90 0.88 PRESENT 3-29 100 12.7 54 3.1 1.71 1.90 0.90 INVENTION 3-30 100 19.5 58 2.7 1.73 1.90 0.91 COMPARATIVE 3-31 — 0 13 13 1.67 2.16 0.77 EXAMPLE 3-32 37 0.9 25 10 1.52 1.95 0.78 EXAMPLE 3-33 84 3.9 47 5.9 1.72 1.95 0.88 OF 3-34 100 8.5 59 2.8 1.78 1.95 0.91 PRESENT 3-35 100 14.6 71 1.5 1.82 1.95 0.93 INVENTION 3-36 100 21.7 63 2.5 1.80 1.95 0.92 COMPARATIVE 3-37 — 0 13 13 1.66 2.16 0.77 EXAMPLE 3-38 21 0.7 25 11 1.51 1.94 0.78 EXAMPLE 3-39 63 2.7 43 6.3 1.71 1.94 0.88 OF 3-40 88 5.6 52 3.2 1.75 1.94 0.90 PRESENT 3-41 100 10.6 62 2.8 1.77 1.94 0.61 INVENTION 3-42 100 17.8 58 3 1.76 1.94 0.91

As listed in Table 9, in examples of the present invention (conditions No. 3-3 to No. 3-12, No. 3-15 to No. 3-18, No. 3-21 to No. 3-24, No. 3-27 to No. 3-30, No. 3-33 to No. 3-36, and No. 3-39 to No. 3-42), the accumulation degree of the {200} planes in the α phase was high at each of the stages of the heat treatment. Further, as listed in Table 10, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were high. As listed in Table 10, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the α phase was not less than 30% nor more than 99% and the accumulation degree of the {222} planes in the α phase was not less than 0.01% nor more than 30% were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more. That is, according to the examples of the present invention, an excellent magnetic property was obtained.

On the other hand, in the conditions No. 3-1 and No. 3-2 being comparative examples, even though the metal layers were formed, a shear strain and a rolling reduction ratio were small, and they did not satisfy the requirement that “after the heating to the A3 point, the accumulation degree of the {200} planes in the α phase is 25% or more and the accumulation degree of the {222} planes in the α phase is 40% or less”, and therefore a high accumulation degree of the {200} planes in the α phase was not obtained and a good magnetic property was not obtained. In the conditions No. 3-13, No. 3-19, No. 3-25, No. 3-31, and No. 3-37 being comparative examples, since the metal layer was not formed, a high accumulation degree of the {200} planes in the α phase was not obtained and a good magnetic property was not obtained even though a large shear strain existed. In the conditions No. 3-14, No. 3-20, No. 3-26, No. 3-32, and No. 3-38 being comparative examples, since the heating temperature was lower than the A3 point, improvement in the accumulation degree of the {200} planes in the α phase owing to the γ-α transformation was not caused, and a good magnetic property was not obtained.

Fourth Experiment

In a fourth experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. 4-1 to condition No. 4-42) were studied.

Base metal plates (silicon steel plates) used in the fourth experiment contained components of the composition N listed in Table 11 and inevitable impurities, with the balance being Fe. The base metal plates were fabricated in such a manner that an ingot was produced by vacuum melting, followed by hot rolling and cold rolling. In the hot rolling, the ingot with a 230 mm thickness heated to 1200° C. was thinned to a 10.0 mm thickness, a 5.0 mm thickness, a 4.0 mm thickness, and a 2.0 mm thickness, whereby four kinds of hot-rolled plates were obtained. An actually measured value of the A3 point at which the base metal plates (silicon steel plates) used in the fourth experiment transformed to a γ single layer was 1010° C.

TABLE 11 COMPONENT ELEMENT (mass %) A3 POINT COMPOSITION C Si Mn Al P N S O OTHERS (° C.) N 0.0002 1.4 0.005 0.1 0.0004 0.005 <0.0004 0.003 1010 O 0.0002 1.1 0.1 0.3 0.0004 0.005 <0.0004 0.003 1005 P 0.0002 1.3 0.2 0.2 0.0004 0.005 <0.0004 0.003 1010 Q 0.0002 0.9 0.15 0.6 0.0004 0.004 <0.0004 0.003 1020 R 0.0003 1.0 0.15 0.4 0.0003 0.004 <0.0004 0.003 1010 S 0.0002 1.5 0.08 0.5 0.0003 0.004 <0.0004 0.003 1080 T 0.0003 0.005 0.12 0.6 0.0004 0.004 <0.0004 0.003 1020 U 0.0003 0.6 0.1 0.65 0.0004 0.004 <0.0004 0.003 Cr: 2% 1000 V 0.0003 0.8 0.1 0.5 0.0004 0.004 <0.0004 0.003 Mo: 1% 1000 W 0.0003 0.2 0.05 0.7 0.0004 0.004 <0.0004 0.003 V: 0.5% 1010

The cold rolling was performed under the following conditions. In the conditions No. 4-1 to 4-7, the hot-rolled plates with a 2.0 mm thickness were pickled to remove scales, and thereafter were rolled to a 0.1 mm thickness. A rolling reduction ratio at this time was 95%. In the conditions No. 4-8 to 4-14, the hot-rolled plates with a 4.0 mm thickness were pickled to remove scales, and thereafter were rolled to a 0.1 mm thickness. A rolling reduction ratio at this time was 97.5%. In the conditions No. 4-15 to 4-21, the hot-rolled steel plates with a 2.0 mm thickness were subjected to shot blasting as hard surface machining on both surfaces, and thereafter were rolled to a 0.1 mm thickness. A rolling reduction ratio at this time was 95%. In the shot blasting, iron beads with a 1 mm to 3 mm diameter were made to continuously collide with the both surfaces of the base metal plates for 10 seconds each. In the conditions No. 4-22 to 4-28, the hot-rolled plates with a 5.0 mm thickness were pickled to remove scales and thereafter were rolled to a 0.25 mm thickness. A rolling reduction ratio at this time was 95%. In the conditions No. 4-29 to 4-35, the hot-rolled plates with a 10.0 mm thickness were pickled to remove scales, and thereafter were rolled to a 0.25 mm thickness. A rolling reduction ratio at this time was 97.5%. In the conditions No. 4-36 to 4-42, the hot-rolled plates with a 5.0 mm thickness were subjected to shot blasting as hard surface machining on both surfaces and thereafter were cold-rolled to a 0.25 mm thickness. A rolling reduction ratio at this time was 95%. In this shot blasting, iron beads with a 1 mm to 3 mm diameter were made to continuously collide with the both surfaces of the base metal plates for ten seconds each.

Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 μm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 12.

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the α phase was within a 17% to 24% range in each of the base metal plates.

Thereafter, Al layers as the metal layers were formed on the front surface and the rear surface of each of the base metal plates by a vapor deposition method, except in the conditions No. 4-1, No. 4-8, No. 4-15, No. 4-22, No. 4-29, and No. 4-36. Thickness of each of the Al layers (total thickness on the both surfaces) is listed in Table 12.

Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200}planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 12.

TABLE 12 BASE METAL PLATE REDUCTION DISLOCATION METAL LAYER CONDITION COMPO- RATE DENSTTY THICKNESS THICKNESS No. SITION BLASTING (%) (m/m³) (μm) ELEMENT (μm) COMPARATIVE 4-1 N WITHOUT 95 1 × 10¹⁵ 100 NONE EXAMPLE EXAMPLE 4-2 N WITHOUT 95 1 × 10¹⁵ 100 Al 9 OF 4-3 N WITHOUT 95 1 × 10¹⁵ 100 Al 9 PRESENT 4-4 N WITHOUT 95 1 × 10¹⁵ 100 Al 9 INVENTION 4-5 N WITHOUT 95 1 × 10¹⁵ 100 Al 9 4-6 N WITHOUT 95 1 × 10¹⁵ 100 Al 9 4-7 N WITHOUT 95 1 × 10¹⁵ 100 Al 9 COMPARATIVE 4-8 N WITHOUT 97.5 1 × 10¹⁶ 100 NONE EXAMPLE EXAMPLE 4-9 N WITHOUT 97.5 1 × 10¹⁶ 100 Al 9 OF 4-10 N WITHOUT 97.5 1 × 10¹⁶ 100 Al 9 PRESENT 4-11 N WITHOUT 97.5 1 × 10¹⁶ 100 Al 9 INVENTION 4-12 N WITHOUT 97.5 1 × 10¹⁶ 100 Al 9 4-13 N WITHOUT 97.5 1 × 10¹⁶ 100 Al 9 4-14 N WITHOUT 97.5 1 × 10¹⁶ 100 Al 9 COMPARATIVE 4-15 N WITH 95 8 × 10¹⁶ 100 NONE EXAMPLE EXAMPLE 4-18 N WITH 95 8 × 10¹⁶ 100 Al 9 OF 4-17 N WITH 95 8 × 10¹⁶ 100 Al 9 PRESENT 4-18 N WITH 95 8 × 10¹⁶ 100 Al 9 INVENTION 4-19 N WITH 95 8 × 10¹⁶ 100 Al 9 4-20 N WITH 95 8 × 10¹⁶ 100 Al 9 4-21 N WITH 95 8 × 10¹⁶ 100 Al 9 COMPARATIVE 4-22 N WITHOUT 95 1 × 10¹⁵ 250 NONE EXAMPLE EXAMPLE 4-23 N WITHOUT 95 1 × 10¹⁵ 250 Al 22 OF 4-24 N WITHOUT 95 1 × 10¹⁵ 250 Al 22 PRESENT 4-25 N WITHOUT 95 1 × 10¹⁵ 250 Al 22 INVENTION 4-26 N WITHOUT 95 1 × 10¹⁵ 250 Al 22 4-27 N WITHOUT 95 1 × 10¹⁵ 250 Al 22 4-28 N WITHOUT 95 1 × 10¹⁵ 250 Al 22 COMPARATIVE 4-29 N WITHOUT 97.5 1 × 10¹⁵ 250 NONE EXAMPLE EXAMPLE 4-30 N WITHOUT 97.5 1 × 10¹⁶ 250 Al 22 OF 4-31 N WITHOUT 97.5 1 × 10¹⁶ 250 Al 22 PRESENT 4-32 N WITHOUT 97.5 1 × 10¹⁶ 250 Al 22 INVENTION 4-33 N WITHOUT 97.5 1 × 10¹⁶ 250 Al 22 4-34 N WITHOUT 97.5 1 × 10¹⁶ 250 Al 22 4-35 N WITHOUT 97.5 1 × 10¹⁶ 250 Al 22 COMPARATIVE 4-36 N WITH 95 8 × 10¹⁶ 250 NONE EXAMPLE EXAMPLE 4-37 N WITH 95 8 × 10¹⁶ 250 Al 22 OF 4-38 N WITH 95 8 × 10¹⁶ 250 Al 22 PRESENT 4-39 N WITH 95 8 × 10¹⁶ 250 Al 22 INVENTION 4-40 N WITH 95 8 × 10¹⁶ 250 Al 22 4-41 N WITH 95 8 × 10¹⁶ 250 Al 22 4-42 N WITH 95 8 × 10¹⁶ 250 Al 22 FIRST SAMPLE ACCUMULATION ACCUMULATION SECOND SAMPLE HETING MEASURED DEGREE OF DEGREE OF KEEPING KEEPING CONDITION RATE TEMPERATURE {200} PLANE {22} PLANE TEMPERATURE TIME No. (° C./s) (° C.) (%) (%) (° C.) (s) COMPARATIVE 4-1 10 1010 16 14 1050 2 EXAMPLE EXAMPLE 4-2 10 1010 26 14 1010 2 OF 4-3 10 1010 26 14 1050 2 PRESENT 4-4 10 1010 26 14 1050 5 INVENTION 4-5 10 1010 26 14 1050 30 4-6 10 1010 26 14 1050 120 4-7 10 1010 26 14 1050 360 COMPARATIVE 4-8 10 1010 16 14 1050 2 EXAMPLE EXAMPLE 4-9 10 1010 40 3.8 1010 2 OF 4-10 10 1010 40 3.8 1050 2 PRESENT 4-11 10 1010 40 3.8 1050 5 INVENTION 4-12 10 1010 40 3.8 1050 30 4-13 10 1010 40 3.8 1050 120 4-14 10 1010 40 3.8 1050 360 COMPARATIVE 4-15 10 1010 15 13 1050 2 EXAMPLE EXAMPLE 4-18 10 1010 59 2.9 1050 2 OF 4-17 10 1010 59 2.9 1050 2 PRESENT 4-18 10 1010 59 2.9 1050 5 INVENTION 4-19 10 1010 59 2.9 1050 30 4-20 10 1010 59 2.9 1050 120 4-21 10 1010 59 2.9 1050 360 COMPARATIVE 4-22 10 1010 16 14 1010 2 EXAMPLE EXAMPLE 4-23 10 1010 26 14 1010 2 OF 4-24 10 1010 27 13 1100 3 PRESENT 4-25 10 1010 27 13 1100 7 INVENTION 4-26 10 1010 27 13 1100 35 4-27 10 1010 27 13 1100 140 4-28 10 1010 27 13 1100 420 COMPARATIVE 4-29 10 1010 16 14 1010 2 EXAMPLE EXAMPLE 4-30 10 1010 40 3.8 1010 2 OF 4-31 10 1010 42 3.2 1100 3 PRESENT 4-32 10 1010 42 3.2 1100 7 INVENTION 4-33 10 1010 42 3.2 1100 35 4-34 10 1010 42 3.2 1100 140 4-35 10 1010 42 3.2 1100 420 COMPARATIVE 4-36 10 1010 15 13 1010 2 EXAMPLE EXAMPLE 4-37 10 1010 59 2.9 1050 2 OF 4-38 10 1010 58 2.8 1100 3 PRESENT 4-39 10 1010 58 2.8 1100 7 INVENTION 4-40 10 1010 58 2.8 1100 35 4-41 10 1010 58 2.8 1100 140 4-42 10 1010 58 2.8 1100 420 SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION COOL- ACCUMULATION ACCUMULATION DEGREE OF DEGREE OF ING DIS- DEGREE OF DEGREE OF CONDITION {200} PLANE {222} PLANE RATE TANCE {200} PLANE {222} PLANE No. (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 4-1 13 13 100 50 13 13 EXAMPLE EXAMPLE 4-2 30 11 100 54 30 11 OF 4-3 31 10 100 54 31 10 PRESENT 4-4 31 10 100 54 31 10 INVENTION 4-5 31 10 100 54 31 10 4-6 31 10 100 54 31 10 4-7 31 10 100 54 31 10 COMPARATIVE 4-8 13 13 100 50 13 13 EXAMPLE EXAMPLE 4-9 45 5.2 100 54 45 5.2 OF 4-10 53 2.7 100 54 53 2.8 PRESENT 4-11 53 2.7 100 54 53 2.8 INVENTION 4-12 53 2.7 100 54 53 2.8 4-13 53 2.7 100 54 53 2.8 4-14 53 2.7 100 54 53 2.8 COMPARATIVE 4-15 13 13 100 50 13 13 EXAMPLE EXAMPLE 4-18 62 2.1 100 54 62 2.1 OF 4-17 75 1.3 100 54 75 1.3 PRESENT 4-18 75 1.3 100 54 75 1.3 INVENTION 4-19 75 1.3 100 54 75 1.3 4-20 75 1.3 100 54 75 1.3 4-21 75 1.3 100 54 75 1.3 COMPARATIVE 4-22 13 13 100 125 13 13 EXAMPLE EXAMPLE 4-23 30 11 100 136 30 11 OF 4-24 32 9 100 136 32 9 PRESENT 4-25 32 9 100 136 32 9 INVENTION 4-26 32 9 100 136 32 9 4-27 32 9 100 135 32 9 4-28 32 9 100 136 32 9 COMPARATIVE 4-29 13 13 100 125 13 13 EXAMPLE EXAMPLE 4-30 44 4.8 100 136 44 4.8 OF 4-31 56 2.1 100 136 56 2.1 PRESENT 4-32 56 2.1 100 136 56 2.1 INVENTION 4-33 56 2.1 100 136 56 2.1 4-34 56 2.1 100 136 56 2.1 4-35 56 2.1 100 136 56 2.1 COMPARATIVE 4-36 13 13 100 125 13 13 EXAMPLE EXAMPLE 4-37 61 2.3 100 136 61 2.3 OF 4-38 82 0.8 100 136 82 0.8 PRESENT 4-39 82 0.8 100 136 82 0.8 INVENTION 4-40 82 0.8 108 136 82 0.8 4-41 82 0.8 100 136 82 0.8 4-42 82 0.8 100 138 82 0.8

Further, an alloying ratio of the metal layer and a ratio of an α single phase region in each Fe-based metal plate were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass % or less and the content of ferrite former was 99.5 mass % or more was regarded as an alloy layer. Further, a region where the Al content was 0.9 mass % or more was regarded as the α single phase region, and a ratio of the α single phase region was found from the aforesaid expression (4). Results of these are listed in Table 13.

Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss W10/1k (W10/100) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 13.

TABLE 13 RATIO OF ACCUMULATION ACCUMULATION ALLOYING α SINGLE DEGREE OF DEGREE OF CONDITION RATE PHASE {200} PLANE {222} PLANE B50 Bs W10/1k No. (%) (%) (%) (%) (T) (T) B50/Bs (W/kg) COMPARATIVE 4-1 0 0 13 13 1.60 2.05 0.78 92 EXAMPLE EXAMPLE 4-2 9 0.1 30 11 1.74 2.05 0.85 65 OF 4-3 82 1.5 31 10 1.74 2.05 0.85 57 PRESENT 4-4 95 8.2 30 10 1.74 2.05 0.85 44 INVENTION 4-5 100 35 30 10 1.74 2.05 0.85 37 4-6 100 73 30 10 1.74 2.05 0.85 43 4-7 100 87 30 10 1.74 2.05 0.85 58 COMPARATIVE 4-8 0 0 13 13 1.60 2.05 0.78 90 EXAMPLE EXAMPLE 4-9 10 0.3 45 5.2 1.78 2.05 0.87 63 OF 4-10 64 2.6 53 2.7 1.85 2.05 0.90 57 PRESENT 4-11 94 7.8 53 2.7 1.87 2.05 0.91 42 INVENTION 4-12 100 42 53 2.7 1.85 2.05 0.90 33 4-13 100 71 53 2.7 1.85 2.05 0.90 38 4-14 100 95 53 2.7 1.87 2.05 0.91 53 COMPARATIVE 4-15 0 0 13 13 1.62 2.05 0.79 92 EXAMPLE EXAMPLE 4-16 8 0.2 62 2.1 1.89 2.05 0.92 62 OF 4-17 67 1.2 75 1.3 1.95 2.05 0.95 48 PRESENT 4-18 89 5.9 75 1.4 1.93 2.05 0.94 41 INVENTION 4-19 100 37 75 1.3 1.95 2.05 0.95 28 4-20 100 72 76 1.4 1.97 2.05 0.96 33 4-21 100 87 75 1.7 1.95 2.05 0.95 48 COMPARATIVE 4-22 0 0 13 13 1.60 2.05 0.78 98 EXAMPLE EXAMPLE 4-23 7 0.5 30 11 1.74 2.05 0.85 63 OF 4-24 57 1.2 32 9 1.74 2.05 0.85 56 PRESENT 4-25 87 6.7 32 9 1.74 2.05 0.85 45 INVENTION 4-26 100 45 32 9 1.74 2.05 0.85 37 4-27 100 72 32 9 1.74 2.05 0.85 42 4-28 100 92 32 9 1.74 2.05 0.85 57 COMPARATIVE 4-29 0 0 13 13 1.60 2.05 0.78 96 EXAMPLE EXAMPLE 4-30 6 0.3 44 4.8 1.80 2.05 0.88 65 OF 4-31 54 1.3 56 2.1 1.87 2.05 0.91 52 PRESENT 4-32 78 6.1 56 2.1 1.85 2.05 0.90 41 INVENTION 4-33 100 38 56 2.2 1.87 2.05 0.91 32 4-34 100 71 56 2.1 1.85 2.05 0.90 38 4-35 100 91 56 2.2 1.87 2.05 0.91 54 COMPARATIVE 4-36 0 0 13 13 1.62 2.05 0.79 101 EXAMPLE EXAMPLE 4-37 8 0.2 61 2.3 1.91 2.05 0.93 61 OF 4-38 70 2.3 82 0.8 1.95 2.05 0.95 46 PRESENT 4-39 91 7.1 82 0.8 1.95 2.05 0.95 40 INVENTION 4-40 100 41 82 0.8 1.97 2.05 0.96 26 4-41 100 76 82 0.8 1.95 2.05 0.95 32 4-42 100 100 82 0.8 1.97 2.05 0.96 48

As listed in Table 12, in examples of the present invention (conditions No. 4-2 to No. 4-7, No. 4-9 to No. 4-14, No. 4-16 to No. 4-21, No. 4-23 to No. 4-28, No. 4-30 to No. 4-35, No. 4-37 to No. 4-42), the accumulation degree of the {200} planes in the α phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 13, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were within the desirable ranges of the present invention. As listed in Table 13, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the α phase was 30% or more and the accumulation degree of the {222} planes in the α phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more.

In the examples of the present invention, when the ratio of the α single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss W10/1k maintained a higher property level. Further, it could be confirmed that the core loss W10/1k has a still better property level when the ratio of the α single phase region is not less than 5% nor more than 80%.

Fifth Experiment

In a fifth experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. 5-1 to condition No. 5-42) were studied.

Base metal plates (silicon steel plates) used in the fifth experiment contained components of the composition O listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the fifth experiment transformed to a γ single phase was 1005° C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 5-1 to the condition No. 5-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively.

Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 μm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 14.

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the α phase was within a 17% to 24% range in each of the base metal plates.

Thereafter, Si layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by a vapor deposition method, except in the conditions No. 5-1, No. 5-8, No. 5-15, No. 5-22, No. 5-29, and No. 5-36. Thickness of each of the Si layers (total thickness on the both surfaces) is listed in Table 14.

Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 14.

TABLE 14 BASE METAL PLATE REDUCTION DISLOCATION METAL LAYER CONDITION COMPO- RATE DENSITY THICKNESS THICKNESS No. SITION BLASTING (%) (m/m³) (μm) ELEMENT (μm) COMPARATIVE 5-1 O WITHOUT 95 1 × 10¹⁵ 100 NONE EXAMPLE EXAMPLE 5-2 O WITHOUT 95 1 × 10¹⁵ 100 Si 10 OF 5-3 O WITHOUT 95 1 × 10¹⁵ 100 Si 10 PRESENT 5-4 O WITHOUT 95 1 × 10¹⁵ 100 Si 10 INVENTION 5-5 O WITHOUT 95 1 × 10¹⁵ 100 Si 10 5-6 O WITHOUT 95 1 × 10¹⁵ 100 Si 10 5-7 O WITHOUT 95 1 × 10¹⁵ 100 Si 10 COMPARATIVE 5-8 O WITHOUT 97.5 1 × 10¹⁵ 100 NONE EXAMPLE EXAMPLE 5-9 O WITHOUT 97.5 1 × 10¹⁵ 100 Si 10 OF 5-10 O WITHOUT 97.5 1 × 10¹⁵ 100 Si 10 PRESENT 5-11 O WITHOUT 97.5 1 × 10¹⁵ 100 Si 10 INVENTION 5-12 O WITHOUT 97.5 1 × 10¹⁵ 100 Si 10 5-13 O WITHOUT 97.5 1 × 10¹⁵ 100 Si 10 5-14 O WITHOUT 97.5 1 × 10¹⁵ 100 Si 10 COMPARATIVE 5-15 O WITH 95 8 × 10¹⁵ 100 NONE EXAMPLE EXAMPLE 5-16 O WITH 95 8 × 10¹⁵ 100 Si 10 OF 5-17 O WITH 95 8 × 10¹⁵ 100 Si 10 PRESENT 5-18 O WITH 95 8 × 10¹⁵ 100 Si 10 INVENTION 5-19 O WITH 95 8 × 10¹⁵ 100 Si 10 5-20 O WITH 95 8 × 10¹⁵ 100 Si 10 5-21 O WITH 95 8 × 10¹⁵ 100 Si 10 COMPARATIVE 5-22 O WITHOUT 95 1 × 10¹⁵ 250 NONE EXAMPLE EXAMPLE 5-23 O WITHOUT 95 1 × 10¹⁵ 250 Si 25 OF 5-24 O WITHOUT 95 1 × 10¹⁵ 250 Si 25 PRESENT 5-25 O WITHOUT 95 1 × 10¹⁵ 250 Si 25 INVENTION 5-26 O WITHOUT 95 1 × 10¹⁵ 250 Si 25 5-27 O WITHOUT 95 1 × 10¹⁵ 250 Si 25 5-28 O WITHOUT 95 1 × 10¹⁵ 250 Si 25 COMPARATIVE 5-29 O WITHOUT 97.5 1 × 10¹⁶ 250 NONE EXAMPLE EXAMPLE 5-30 O WITHOUT 97.5 1 × 10¹⁶ 250 Si 25 OF 5-31 O WITHOUT 97.5 1 × 10¹⁶ 250 Si 25 PRESENT 5-32 O WITHOUT 97.5 1 × 10¹⁶ 250 Si 25 INVENTION 5-33 O WITHOUT 97.5 1 × 10¹⁶ 250 Si 25 5-34 O WITHOUT 97.5 1 × 10¹⁶ 250 Si 25 5-35 O WITHOUT 97.5 1 × 10¹⁶ 250 Si 25 COMPARATIVE 5-36 O WITH 95 8 × 10¹⁶ 250 NONE EXAMPLE EXAMPLE 5-37 O WITH 95 8 × 10¹⁶ 250 Si 25 OF 5-38 O WITH 95 8 × 10¹⁶ 250 Si 25 PRESENT 5-39 O WITH 85 8 × 10¹⁶ 250 Si 25 INVENTION 5-40 O WITH 95 8 × 10¹⁶ 250 Si 25 5-41 O WITH 95 8 × 10¹⁶ 250 Si 25 5-42 O WITH 95 8 × 10¹⁶ 250 Si 25 FIRST SAMPLE ACCUMULATION ACCUMULATION SECOND SAMPLE HETING MEASURED DEGREE OF DEGREE OF KEEPING KEEPING CONDITION RATE TEMPERATURE {200} PLANE {222} PLANE TEMPERATURE TIME No. (° C./s) (° C.) (%) (%) (° C.) (s) COMPARATIVE 5-1 20 1005 15 14 1050 2 EXAMPLE EXAMPLE 5-2 20 1005 25 15 1005 2 OF 5-3 20 1005 25 15 1050 2 PRESENT 5-4 20 1005 25 15 1050 5 INVENTION 5-5 20 1005 25 15 1050 30 5-6 20 1005 25 15 1050 120 5-7 20 1005 25 15 1050 360 COMPARATIVE 5-8 20 1005 17 13 1050 2 EXAMPLE EXAMPLE 5-9 20 1005 38 4.1 1005 2 OF 5-10 20 1005 38 4.1 1050 2 PRESENT 5-11 20 1005 38 4.1 1050 5 INVENTION 5-12 20 1005 38 4.1 1050 30 5-13 20 1005 38 4.1 1050 120 5-14 20 1005 38 4.1 1050 360 COMPARATIVE 5-15 20 1005 15 13 1050 2 EXAMPLE EXAMPLE 5-16 20 1005 56 2.8 1005 2 OF 5-17 20 1005 56 2.8 1050 2 PRESENT 5-18 20 1005 56 2.8 1050 5 INVENTION 5-19 20 1005 56 2.8 1050 30 5-20 20 1005 56 2.8 1050 120 5-21 20 1005 56 2.8 1050 360 COMPARATIVE 5-22 20 1005 16 14 1100 2 EXAMPLE EXAMPLE 5-23 20 1005 26 14 1005 2 OF 5-24 20 1005 26 14 1100 3 PRESENT 5-25 20 1005 26 14 1100 7 INVENTION 5-26 20 1005 26 14 1100 35 5-27 20 1005 26 14 1100 140 5-28 20 1005 26 14 1100 420 COMPARATIVE 5-29 20 1005 17 13 1100 2 EXAMPLE EXAMPLE 5-30 20 1005 39 3.8 1005 2 OF 5-31 20 1005 39 3.8 1100 3 PRESENT 5-32 20 1005 39 3.8 1100 7 INVENTION 5-33 20 1005 39 3.8 1100 35 5-34 20 1005 39 3.8 1100 140 5-35 20 1005 39 3.8 1100 420 COMPARATIVE 5-36 10 1005 17 14 1100 2 EXAMPLE EXAMPLE 5-37 20 1005 54 2.7 1005 2 OF 5-38 20 1005 54 2.7 1100 3 PRESENT 5-39 20 1005 54 2.7 1100 7 INVENTION 5-40 20 1005 54 2.7 1100 35 5-41 20 1005 54 2.7 1100 140 5-42 20 1005 54 2.7 1100 420 SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION COOL- ACCUMULATION ACCUMULATION DEGREE OF DEGREE OF ING DIS- DEGREE OF DEGREE OF CONDITION {200} PLANE {222} PLANE RATE TANCE {200} PLANE {222} PLANE No. (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 5-1 13 13 100 50 13 13 EXAMPLE EXAMPLE 5-2 31 12 100 54 31 12 OF 5-3 32 9 20 54 32 9 PRESENT 5-4 32 9 20 54 32 9 INVENTION 5-5 32 9 20 54 32 9 5-6 32 9 20 54 32 9 5-7 32 9 20 54 32 9 COMPARATIVE 5-8 13 13 100 50 13 13 EXAMPLE EXAMPLE 5-9 43 5.7 100 54 43 5.7 OF 5-10 55 2.1 20 54 55 2.1 PRESENT 5-11 55 2.1 20 54 55 2.1 INVENTION 5-12 55 2.1 20 54 55 2.1 5-13 55 2.1 20 54 55 2.1 5-14 55 2.1 20 54 55 2.1 COMPARATIVE 5-15 13 13 100 50 13 13 EXAMPLE EXAMPLE 5-16 58 2.4 100 54 58 2.4 OF 5-17 78 1.1 20 54 78 1.1 PRESENT 5-18 78 1.1 20 54 78 1.1 INVENTION 5-19 78 1.1 20 54 78 1.1 5-20 78 1.1 20 54 78 1.1 5-21 78 1.1 20 54 78 1.1 COMPARATIVE 5-22 13 13 100 125 13 13 EXAMPLE EXAMPLE 5-23 30 12 100 136 30 12 OF 5-24 31 10 20 136 31 10 PRESENT 5-25 31 10 20 136 31 10 INVENTION 5-26 31 10 20 136 31 10 5-27 31 10 20 136 31 10 5-28 31 10 20 136 31 10 COMPARATIVE 5-29 13 13 100 125 13 13 EXAMPLE EXAMPLE 5-30 42 5 100 136 42 5 OF 5-31 58 1.9 20 136 58 1.9 PRESENT 5-32 58 1.9 20 136 58 1.9 INVENTION 5-33 58 1.9 20 136 58 1.9 5-34 58 1.9 20 136 58 1.9 5-35 58 1.9 20 136 58 1.9 COMPARATIVE 5-36 13 13 100 125 13 13 EXAMPLE EXAMPLE 5-37 52 2.1 100 136 62 2.1 OF 5-38 87 0.3 20 136 87 0.3 PRESENT 5-39 87 0.3 20 136 87 0.3 INVENTION 5-40 87 0.3 20 136 87 0.3 5-41 87 0.3 20 136 87 0.3 5-42 87 0.3 20 136 87 0.3

Further, an alloying ratio of the metal layer and a ratio of an α single phase region in each Fe-based metal plate were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass % or less and the content of ferrite former was 99.5 mass % or more was regarded as an alloy layer. Further, a region where the Si content was 1.9 mass % or more was regarded as the α single phase region, and a ratio of the α single phase region was found from the aforesaid expression (4). Results of these are listed in Table 15.

Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss W10/1k (W10/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 15.

TABLE 15 RATIO OF ACCUMULATION ACCUMULATION ALLOYING α SINGLE DEGREE OF DEGREE OF CONDITION RATE PHASE {200} PLANE {222} PLANE B50 Bs W10/1k No. (%) (%) (%) (%) (T) (T) B50/Bs (W/kg) COMPARATIVE 5-1 0 0 13 13 1.61 2.07 0.78 93 EXAMPLE EXAMPLE 5-2 8 0.2 31 12 1.76 2.07 0.85 64 OF 5-3 67 2.1 32 9 1.78 2.07 0.86 59 PRESENT 5-4 89 7.6 32 9 1.78 2.07 0.86 45 INVENTION 5-5 100 40 32 9 1.78 2.07 0.86 38 5-6 100 71 32 9 1.78 2.07 0.86 42 5-7 100 95 32 9 1.78 2.07 0.86 59 COMPARATIVE 5-8 0 0 13 13 1.61 2.07 0.78 91 EXAMPLE EXAMPLE 5-9 10 0.3 43 5.7 1.80 2.07 0.87 62 OF 5-10 51 1.2 55 2.1 1.88 2.07 0.91 53 PRESENT 5-11 82 5.9 55 2.1 1.88 2.07 0.91 41 INVENTION 5-12 100 38 55 2.1 1.88 2.07 0.91 32 5-13 100 72 55 2.1 1.88 2.07 0.91 35 5-14 100 89 55 2.1 1.88 2.07 0.91 53 COMPARATIVE 5-15 0 0 13 13 1.64 2.07 0.79 94 EXAMPLE EXAMPLE 5-18 8 0.2 58 2.4 1.90 2.07 0.92 61 OF 5-17 72 2.3 78 1.1 1.99 2.07 0.96 47 PRESENT 5-18 87 6.8 78 1.1 1.99 2.07 0.96 40 INVENTION 5-19 100 42 78 1.1 1.99 2.07 0.96 29 5-20 100 62 78 1.1 1.99 2.07 0.96 32 5-21 100 90 78 1.1 1.99 2.07 0.96 48 COMPARATIVE 5-22 0 0 13 13 1.61 2.07 0.78 102 EXAMPLE EXAMPLE 5-23 7 0.5 30 12 1.76 2.07 0.85 61 OF 5-24 62 1.6 31 10 1.78 2.07 0.86 59 PRESENT 5-25 86 7.1 31 10 1.78 2.07 0.86 43 INVENTION 5-26 100 32 31 10 1.78 2.07 0.86 36 5-27 100 63 31 10 1.78 2.07 0.86 41 5-28 100 100 31 10 1.78 2.07 0.86 57 COMPARATIVE 5-29 0 0 13 13 1.61 2.07 0.78 97 EXAMPLE EXAMPLE 5-30 6 0.3 42 5 1.82 2.07 0.88 62 OF 5-31 46 1.1 58 1.9 1.86 2.07 0.90 53 PRESENT 5-32 82 8.3 58 1.9 1.86 2.07 0.90 41 INVENTION 5-33 100 43 58 1.9 1.86 2.07 0.90 33 5-34 100 72 58 1.9 1.86 2.07 0.90 37 5-35 100 98 58 1.9 1.86 2.07 0.90 54 COMPARATIVE 5-36 0 0 13 13 1.64 2.07 0.79 98 EXAMPLE EXAMPLE 5-37 8 0.2 62 2.1 1.93 2.07 0.93 64 OF 5-38 69 3.2 87 0.3 1.99 2.07 0.96 46 PRESENT 5-39 89 8.1 87 0.3 1.99 2.07 0.96 40 INVENTION 5-40 100 45 87 0.3 1.99 2.07 0.96 27 5-41 100 68 87 0.3 1.99 2.07 0.96 34 5-42 100 92 87 0.3 1.99 2.07 0.96 46

As listed in Table 14, in examples of the present invention (conditions No. 5-2 to No. 5-7, No. 5-9 to No. 5-14, No. 5-16 to No. 5-21, No. 5-23 to No. 5-28, No. 5-30 to No. 5-35, No. 5-37 to No. 5-42), the accumulation degree of the {200} planes in the α phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 15, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were within the desirable ranges of the present invention. As listed in Table 15, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the α phase was 30% or more and the accumulation degree of the {222} planes in the α phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more.

In the examples of the present invention, when the ratio of the α single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss W10/1k maintained a higher property level. Further, it could be confirmed that the core loss W10/1k has a still better property level when the ratio of the α single phase region is not less than 5% nor more than 80%.

Sixth Experiment

In a sixth experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. 6-1 to condition No. 6-42) were studied.

Base metal plates (silicon steel plates) used in the sixth experiment contained components of the composition P listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the sixth experiment transformed to a γ single phase was 1010° C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 6-1 to the condition No. 6-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively.

Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 μm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 16.

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the α phase was within a 17% to 24% range in each of the base metal plates.

Thereafter, Sn layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by an electroplating method, except in the conditions No. 6-1, No. 6-8, No. 6-15, No. 6-22, No. 6-29, and No. 6-36. Thickness of each of the Sn layers (total thickness on the both surfaces) is listed in Table 16.

Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 16.

TABLE 16 BASE METAL PLATE REDUCTION DISLOCATION METAL LAYER CONDITION COMPO- RATE DENSITY THICKNESS THICKNESS No. SITION BLASTING (%) (m/m³) (μm) ELEMENT (μm) COMPARATIVE 6-1 P WITHOUT 95 1 × 10¹⁵ 100 NONE EXAMPLE EXAMPLE 6-2 P WITHOUT 95 1 × 10¹⁵ 100 Sn 3.2 OF 6-3 P WITHOUT 95 1 × 10¹⁵ 100 Sn 3.2 PRESENT 6-4 P WITHOUT 95 1 × 10¹⁵ 100 Sn 3.2 INVENTION 6-5 P WITHOUT 95 1 × 10¹⁵ 100 Sn 3.2 6-6 P WITHOUT 95 1 × 10¹⁵ 100 Sn 3.2 6-7 P WITHOUT 95 1 × 10¹⁵ 100 Sn 3.2 COMPARATIVE 6-8 P WITHOUT 97.5 1 × 10¹⁵ 100 NONE EXAMPLE EXAMPLE 6-9 P WITHOUT 97.5 1 × 10¹⁶ 100 Sn 3.2 OF 6-10 P WITHOUT 97.5 1 × 10¹⁶ 100 Sn 3.2 PRESENT 6-11 P WITHOUT 97.5 1 × 10¹⁶ 100 Sn 3.2 INVENTION 6-12 P WITHOUT 97.5 1 × 10¹⁶ 100 Sn 3.2 6-13 P WITHOUT 97.5 1 × 10¹⁶ 100 Sn 3.2 6-14 P WITHOUT 97.5 1 × 10¹⁶ 100 Sn 3.2 COMPARATIVE 6-15 P WITH 95 8 × 10¹⁶ 100 NONE EXAMPLE EXAMPLE 6-16 P WITH 95 8 × 10¹⁶ 100 Sn 3.2 OF 6-17 P WITH 95 8 × 10¹⁶ 100 Sn 3.2 PRESENT 6-18 P WITH 95 8 × 10¹⁶ 100 Sn 3.2 INVENTION 6-19 P WITH 95 8 × 10¹⁶ 100 Sn 3.2 6-20 P WITH 95 8 × 10¹⁶ 100 Sn 3.2 6-21 P WITH 95 8 × 10¹⁶ 100 Sn 3.2 COMPARATIVE 6-22 P WITHOUT 95 1 × 10¹⁵ 250 NONE EXAMPLE EXAMPLE 6-23 P WITHOUT 95 1 × 10¹⁵ 250 Sn 8 OF 6-24 P WITHOUT 65 1 × 10¹⁵ 250 Sn 8 PRESENT 6-25 P WITHOUT 95 1 × 10¹⁵ 250 Sn 8 INVENTION 6-26 P WITHOUT 95 1 × 10¹⁵ 250 Sn 8 6-27 P WITHOUT 95 1 × 10¹⁵ 250 Sn 8 6-28 P WITHOUT 95 1 × 10¹⁵ 250 Sn 8 COMPARATIVE 6-29 P WITHOUT 97.5 1 × 10¹⁵ 250 NONE EXAMPLE EXAMPLE 6-30 P WITHOUT 97.5 1 × 10¹⁵ 250 Sn 8 OF 6-31 P WITHOUT 97.5 1 × 10¹⁵ 250 Sn 8 PRESENT 6-32 P WITHOUT 97.5 1 × 10¹⁵ 250 Sn 8 INVENTION 6-33 P WITHOUT 97.5 1 × 10¹⁵ 250 Sn 8 6-34 P WITHOUT 97.5 1 × 10¹⁵ 250 Sn 8 6-35 P WITHOUT 97.5 1 × 10¹⁵ 250 Sn 8 COMPARATIVE 6-36 P WITH 95 8 × 10¹⁵ 250 NONE EXAMPLE EXAMPLE 6-37 P WITH 95 8 × 10¹⁸ 250 Sn 8 OF 6-38 P WITH 95 8 × 10¹⁸ 250 Sn 8 PRESENT 6-39 P WITH 95 8 × 10¹⁸ 250 Sn 8 INVENTION 6-40 P WITH 95 8 × 10¹⁸ 250 Sn 8 6-41 P WITH 95 8 × 10¹⁸ 250 Sn 8 6-42 P WITH 95 8 × 10¹⁸ 250 Sn 8 FIRST SAMPLE ACCUMULATION ACCUMULATION SECOND SAMPLE HETING MEASURED DEGREE OF DEGREE OF KEEPING KEEPING CONDITION RATE TEMPERATURE {200} PLANE {222} PLANE TEMPERATURE TIME No. (° C./s) (° C.) (%) (%) (° C.) (s) COMPARATIVE 6-1 10 1010 18 13 1050 2 EXAMPLE EXAMPLE 6-2 10 1010 26 14 1010 2 OF 6-3 10 1010 26 14 1050 2 PRESENT 6-4 10 1010 26 14 1050 5 INVENTION 6-5 10 1010 26 14 1050 30 6-6 10 1010 26 14 1050 120 6-7 10 1010 26 14 1050 360 COMPARATIVE 6-8 10 1010 18 13 1050 2 EXAMPLE EXAMPLE 6-9 10 1010 35 5 1010 2 OF 6-10 10 1010 35 5 1050 2 PRESENT 6-11 10 1010 35 5 1050 5 INVENTION 6-12 10 1010 35 5 1050 30 6-13 10 1010 35 5 1050 120 6-14 10 1010 35 5 1050 360 COMPARATIVE 6-15 10 1010 18 13 1050 2 EXAMPLE EXAMPLE 6-16 10 1010 60 2.5 1010 2 OF 6-17 10 1010 60 2.5 1050 2 PRESENT 6-18 10 1010 60 2.5 1050 5 INVENTION 6-19 10 1010 60 2.5 1050 30 6-20 10 1010 60 2.5 1050 120 6-21 10 1010 60 2.5 1050 360 COMPARATIVE 6-22 10 1010 18 13 1100 2 EXAMPLE EXAMPLE 6-23 10 1010 25 16 1010 2 OF 6-24 10 1010 25 16 1100 3 PRESENT 6-25 10 1010 25 16 1100 7 INVENTION 6-26 10 1010 25 16 1100 35 6-27 10 1010 25 16 1100 140 6-28 10 1010 25 16 1100 420 COMPARATIVE 6-29 10 1010 18 13 1100 2 EXAMPLE EXAMPLE 6-30 10 1010 37 4.1 1010 2 OF 6-31 10 1010 37 4.1 1100 3 PRESENT 6-32 10 1010 37 4.1 1100 7 INVENTION 6-33 10 1010 37 4.1 1100 35 6-34 10 1010 37 4.1 1100 140 6-35 10 1010 37 4.1 1100 420 COMPARATIVE 6-36 10 1010 18 13 1100 2 EXAMPLE EXAMPLE 6-37 10 1010 57 2.5 1010 2 OF 6-38 10 1010 57 2.5 1100 3 PRESENT 6-39 10 1010 57 2.5 1100 7 INVENTION 6-40 10 1010 57 2.5 1100 35 6-41 10 1010 57 2.5 1100 140 6-42 10 1010 57 2.5 1100 420 SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION COOL- ACCUMULATION ACCUMULATION DEGREE OF DEGREE OF ING DIS- DEGREE OF DEGREE OF CONDITION [200] PLANE [222] PLANE RATE TANCE [200] PLANE {222} PLANE No. (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 6-1 13 13 5 50 13 13 EXAMPLE EXAMPLE 6-2 30 10 5 54 30 10 OF 6-3 33 8 5 54 33 8 PRESENT 6-4 33 8 5 54 33 8 INVENTION 6-5 33 8 5 54 33 8 6-6 33 8 5 54 33 8 6-7 33 8 5 54 33 8 COMPARATIVE 6-8 13 13 5 54 13 13 EXAMPLE EXAMPLE 6-9 43 42 5 54 43 4.2 OF 6-10 54 1.8 5 54 54 1.8 PRESENT 6-11 54 1.8 5 54 54 1.8 INVENTION 6-12 54 1.8 5 54 54 1.8 6-13 54 1.8 5 54 54 1.8 6-14 54 1.8 5 54 54 1.8 COMPARATIVE 6-15 13 13 5 50 13 13 EXAMPLE EXAMPLE 6-16 64 2.2 5 54 64 22 OF 6-17 80 0.9 5 54 80 0.9 PRESENT 6-18 80 0.9 5 54 80 0.9 INVENTION 6-19 80 0.9 5 54 80 0.9 6-20 80 0.9 5 54 80 0.9 6-21 60 0.9 5 54 80 0.9 COMPARATIVE 6-22 13 13 5 125 13 13 EXAMPLE EXAMPLE 6-23 30 10 5 138 30 10 OF 6-24 31 9 5 136 31 9 PRESENT 6-25 31 9 5 138 31 9 INVENTION 6-26 31 9 5 136 31 9 6-27 31 9 5 136 31 9 6-28 31 9 5 136 31 9 COMPARATIVE 6-29 13 13 5 125 13 13 EXAMPLE EXAMPLE 6-30 42 4.9 5 136 42 4.9 OF 6-31 55 2.3 5 136 55 2.3 PRESENT 6-32 55 2.3 5 136 55 2.3 INVENTION 6-33 55 2.3 5 136 55 2.3 6-34 55 2.3 5 136 55 2.3 6-35 55 2.3 5 136 55 2.3 COMPARATIVE 6-36 13 13 5 125 13 13 EXAMPLE EXAMPLE 6-37 62 2.1 5 136 62 2.1 OF 6-38 74 0.3 5 136 74 0.3 PRESENT 6-39 74 0.3 5 136 74 0.3 INVENTION 6-40 74 0.3 5 136 74 0.3 6-41 74 0.3 5 136 74 0.3 6-42 74 0.3 5 136 74 0.3

Further, an alloying ratio of the metal layer and a ratio of an α single phase region in each Fe-based metal plate were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass % or less and the content of ferrite former was 99.5 mass % or more was regarded as an alloy layer. Further, a region where the Sn content was 3.0 mass % or more was regarded as the α single phase region, and a ratio of the α single phase region was found from the aforesaid expression (4). Results of these are listed in Table 17.

Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss W10/1k (W10/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 17.

TABLE 17 ACCUMULATION RATIO OF DEGREE OF ACCUMULATION ALLOYING α SINGLE {2001 DEGREE OF CONDITION RATE PHASE PLANE {222} PLANE B50 Bs W10/1K No. (%) (%) (%) (%) (T) (T) B50/Bs (W/kg) COMPARATIVE 6-1 0 0 13 13 1.61 2.06 0.78 91 EXAMPLE EXAMPLE 6-2 6 0.2 30 10 1.75 2.06 0.85 64 OF 6-3 43 1.8 33 8 1.75 2.06 0.85 56 PRESENT 6-4 78 6.2 33 8 1.75 2.06 0.85 43 INVENTION 6-5 100 38 33 8 1.75 2.06 0.85 38 6-6 100 68 33 8 1.75 2.06 0.85 43 6-7 100 87 33 8 1.75 2.06 0.85 58 COMPARATIVE 6-8 0 0 13 13 1.61 2.06 0.78 92 EXAMPLE EXAMPLE 6-9 7 0.1 43 4.2 1.79 2.06 0.87 61 OF 6-10 65 2.4 54 1.8 1.85 2.06 0.90 52 PRESENT 6-11 85 5.9 54 1.8 1.85 2.06 0.90 43 INVENTION 6-12 100 46 54 1.8 1.85 2.06 0.90 32 6-13 100 72 54 1.8 1.85 2.06 0.90 35 6-14 100 90 54 1.8 1.85 2.06 0.90 52 COMPARATIVE 6-15 0 0 13 13 1.63 2.06 0.79 93 EXAMPLE EXAMPLE 6-16 6 0.2 64 2.2 1.90 2.06 0.92 61 OF 6-17 76 3.5 80 0.9 1.98 2.06 0.96 46 PRESENT 6-18 92 8.2 80 0.9 1.98 2.06 0.96 40 INVENTION 6-19 100 38 80 0.9 1.98 2.06 0.96 28 6-20 100 69 80 0.9 1.98 2.06 0.96 32 6-21 100 85 80 0.9 1.98 2.06 0.96 48 COMPARATIVE 6-22 0 0 13 13 1.61 2.06 0.78 98 EXAMPLE EXAMPLE 6-23 5 0.1 30 10 1.75 2.06 0.85 64 OF 6-24 68 2.2 31 9 1.73 2.06 0.84 59 PRESENT 6-25 84 6.4 31 9 1.73 2.06 0.84 44 INVENTION 6-26 100 35 31 9 1.73 2.06 0.84 39 6-27 100 71 31 9 1.73 2.06 0.84 43 6-28 100 95 31 9 1.73 2.06 0.84 59 COMPARATIVE 6-29 0 0 13 13 1.61 2.06 0.78 103 EXAMPLE EXAMPLE 6-30 5 2 42 4.9 1.81 2.06 0.88 64 OF 6-31 48 1.5 55 2.3 1.87 2.06 0.91 52 PRESENT 6-32 77 6.2 55 2.3 1.87 2.06 0.91 41 INVENTION 6-33 100 40 55 2.3 1.87 2.06 0.91 34 6-34 100 71 55 2.3 1.87 2.06 0.91 38 6-35 100 93 55 2.3 1.87 2.06 0.91 54 COMPARATIVE 6-36 0 0 13 13 1.63 2.06 0.79 98 EXAMPLE EXAMPLE 6-37 7 0.2 62 2.1 1.92 2.06 0.93 63 OF 6-38 57 1.9 74 0.3 1.96 2.06 0.95 46 PRESENT 6-39 79 7.6 74 0.3 1.96 2.06 0.95 42 INVENTION 6-40 100 43 74 0.3 1.96 2.06 0.95 29 6-41 100 74 74 0.3 1.96 2.06 0.95 32 6-42 100 86 74 0.3 1.96 2.06 0.95 47

As listed in Table 16, in examples of the present invention (conditions No. 6-2 to No 6-7, No. 6-9 to No. 6-14, No. 6-16 to No. 6-21, No. 6-23 to No. 6-28, No. 6-30 to No. 6-35, No. 6-37 to No. 6-42), the accumulation degree of the {200} planes in the α phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 17, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were within the desirable ranges of the present invention. As listed in Table 17, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the α phase was 30% or more and the accumulation degree of the {222} planes in the α phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more.

In the examples of the present invention, when the ratio of the α single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss W10/1k maintained a higher property level. Further, it could be confirmed that the core loss W10/1k has a still better property level when the ratio of the α single phase region is not less than 5% nor more than 80%.

Seventh Experiment

In a seventh experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. 7-1 to condition No. 7-42) were studied.

Base metal plates (silicon steel plates) used in the seventh experiment contained components of the composition Q listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the seventh experiment transformed to a γ single phase was 1020° C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 7-1 to the condition No. 7-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively.

Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 μm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 18.

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the α phase was within a 17% to 24% range in each of the base metal plates.

Thereafter, Mo layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by a sputtering method, except in the conditions No. 7-1, No. 7-8, No. 7-15, No. 7-22, No. 7-29, and No. 7-36. Thickness of each of the Mo layers (total thickness on the both surfaces) is listed in Table 18.

Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 18.

TABLE 18 BASE METAL PLATE REDUCTION DISLOCATION METAL LAYER CONDITION COMPO- RATE DENSITY THICKNESS THICKNESS No. SITION BLASTING (%) (m/m³) (μm) ELEMENT (μm) COMPARATIVE 7-1 Q WITHOUT 95 1 × 10¹⁵ 100 NONE EXAMPLE EXAMPLE 7-2 Q WITHOUT 95 1 × 10¹⁵ 100 Mo 2.4 OF 7-3 Q WITHOUT 95 1 × 10¹⁵ 100 Mo 2.4 PRESENT 7-4 Q WITHOUT 95 1 × 10¹⁵ 100 Mo 2.4 INVENTION 7-5 Q WITHOUT 95 1 × 10¹⁵ 100 Mo 2.4 7-6 Q WITHOUT 95 1 × 10¹⁵ 100 Mo 2.4 7-7 Q WITHOUT 95 1 × 10¹⁵ 100 Mo 2.4 COMPARATIVE 7-8 Q WITHOUT 97.5 1 × 10¹⁶ 100 NONE EXAMPLE EXAMPLE 7-9 Q WITHOUT 97.5 1 × 10¹⁶ 100 Mo 2.4 OF 7-10 Q WITHOUT 97.5 1 × 10¹⁶ 100 Mo 2.4 PRESENT 7-11 Q WITHOUT 97.5 1 × 10¹⁶ 100 Mo 2.4 INVENTION 7-12 Q WITHOUT 97.5 1 × 10¹⁶ 100 Mo 2.4 7-13 Q WITHOUT 97.5 1 × 10¹⁶ 100 Mo 2.4 7-14 Q WITHOUT 97.5 1 × 10¹⁶ 100 Mo 2.4 COMPARATIVE 7-15 Q WITH 95 8 × 10¹⁶ 100 NONE EXAMPLE EXAMPLE 7-16 Q WITH 95 8 × 10¹⁶ 100 Mo 2.4 OF 7-17 Q WITH 95 8 × 10¹⁶ 100 Mo 2.4 PRESENT 7-18 Q WITH 95 8 × 10¹⁶ 100 Mo 2.4 INVENTION 7-19 Q WITH 95 8 × 10¹⁶ 100 Mo 2.4 7-20 Q WITH 95 8 × 10¹⁶ 100 Mo 2.4 7-21 Q WITH 95 8 × 10¹⁶ 100 Mo 2.4 COMPARATIVE 7-22 Q WITHOUT 95 1 × 10¹⁵ 250 NONE EXAMPLE EXAMPLE 7-23 Q WITHOUT 95 1 × 10¹⁵ 250 Mo 6 OF 7-24 Q WITHOUT 95 1 × 10¹⁵ 250 Mo 6 PRESENT 7-25 Q WITHOUT 95 1 × 10¹⁵ 250 Mo 6 INVENTION 7-26 Q WITHOUT 95 1 × 10¹⁵ 250 Mo 6 7-27 Q WITHOUT 95 1 × 10¹⁵ 250 Mo 6 7-28 Q WITHOUT 95 1 × 10¹⁵ 250 Mo 6 COMPARATIVE 7-29 Q WITHOUT 97.5 1 × 10¹⁶ 250 NONE EXAMPLE EXAMPLE 7-30 Q WITHOUT 97.5 1 × 10¹⁵ 250 Mo 6 OF 7-31 Q WITHOUT 97.5 1 × 10¹⁵ 250 Mo 6 PRESENT 7-32 Q WITHOUT 97.5 1 × 10¹⁵ 250 Mo 6 INVENTION 7-33 Q WITHOUT 97.5 1 × 10¹⁶ 250 Mo 6 7-34 Q WITHOUT 97.5 1 × 10¹⁶ 250 Mo 6 7-35 Q WITHOUT 97.5 1 × 10¹⁶ 250 Mo 6 COMPARATIVE 7-36 Q WITH 95 8 × 10¹⁶ 250 NONE EXAMPLE EXAMPLE 7-37 Q WITH 95 8 × 10¹⁶ 250 Mo 6 OF 7-38 Q WITH 95 8 × 10¹⁵ 250 Mo 6 PRESENT 7-39 Q WITH 95 8 × 10¹⁶ 250 Mo 6 INVENTION 7-40 Q WITH 95 8 × 10¹⁶ 250 Mo 6 7-41 Q WITH 95 8 × 10¹⁶ 250 Mo 6 7-42 Q WITH 95 8 × 10¹⁶ 250 Mo 6 FIRST SAMPLE ACCUMULATION ACCUMULATION SECOND SAMPLE HETING MEASURED DEGREE OF DEGREE OF KEEPING KEEPING CONDITION RATE TEMPERATURE [200] PLANE [222] PLANE TEMPERATURE TIME No. (° C./s) (° C.) (%) (%) (° C.) (s) COMPARATIVE 7-1 5 1020 17 14 1100 2 EXAMPLE EXAMPLE 7-2 5 1020 27 13 1020 2 OF 7-3 5 1020 27 13 1100 2 PRESENT 7-4 5 1020 27 13 1100 5 INVENTION 7-5 5 1020 27 13 1100 30 7-6 5 1020 27 13 1100 120 7-7 5 1020 27 13 1100 360 COMPARATIVE 7-8 5 1010 17 14 1100 2 EXAMPLE EXAMPLE 7-9 5 1020 32 7 1020 2 OF 7-10 5 1020 32 7 1100 2 PRESENT 7-11 5 1020 32 7 1100 5 INVENTION 7-12 5 1020 32 7 1100 30 7-13 5 1020 32 7 1100 120 7-14 5 1020 32 7 1100 360 COMPARATIVE 7-15 5 1010 17 13 1100 2 EXAMPLE EXAMPLE 7-16 5 1020 53 3.8 1020 2 OF 7-17 5 1020 53 3.8 1100 2 PRESENT 7-18 5 1020 53 3.8 1100 5 INVENTION 7-19 5 1020 53 3.8 1100 30 7-20 5 1020 53 3.8 1100 120 7-21 5 1020 53 3.8 1100 360 COMPARATIVE 7-22 5 1010 18 13 1150 2 EXAMPLE EXAMPLE 7-23 5 1020 26 12 1020 2 OF 7-24 5 1020 26 12 1150 3 PRESENT 7-25 5 1020 26 12 1150 7 INVENTION 7-26 5 1020 26 12 1150 35 7-27 5 1020 26 12 1150 140 7-28 5 1020 26 12 1150 420 COMPARATIVE 7-29 5 1020 18 13 1150 2 EXAMPLE EXAMPLE 7-30 5 1020 35 6 1020 2 OF 7-31 5 1020 35 6 1150 3 PRESENT 7-32 5 1020 35 6 1150 7 INVENTION 7-33 5 1020 35 6 1150 35 7-34 5 1020 35 6 1150 140 7-35 5 1020 35 6 1150 420 COMPARATIVE 7-36 5 1020 18 14 1150 2 EXAMPLE EXAMPLE 7-37 5 1020 54 3.1 1020 2 OF 7-38 5 1020 54 3.1 1150 3 PRESENT 7-39 5 1020 54 3.1 1150 7 INVENTION 7-40 5 1020 54 3.1 1150 35 7-41 5 1020 54 3.1 1150 140 7-42 5 1020 54 3.1 1150 420 SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION COOL- ACCUMULATION ACCUMULATION DEGREE OF DEGREE OF ING DIS- DEGREE OF DEGREE OF CONDITION [200] PLANE [222] PLANE RATE TANCE [200] PLANE [222] PLANE No. (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 7-1 13 13 10 50 13 13 EXAMPLE EXAMPLE 7-2 30 10 10 54 30 10 OF 7-3 30 10 10 54 30 10 PRESENT 7-4 30 10 10 54 30 10 INVENTION 7-5 30 10 10 54 30 10 7-6 30 10 10 54 30 10 7-7 30 10 10 54 30 10 COMPARATIVE 7-8 13 13 10 50 13 13 EXAMPLE EXAMPLE 7-9 41 5.8 10 54 41 5.8 OF 7-10 52 2.2 10 54 52 2.2 PRESENT 7-11 52 2.2 10 54 52 2.2 INVENTION 7-12 52 2.2 10 54 52 2.2 7-13 52 2.2 10 54 52 2.2 7-14 52 2.2 10 54 52 2.2 COMPARATIVE 7-15 13 13 10 50 13 13 EXAMPLE EXAMPLE 7-16 60 2.5 10 54 60 2.5 OF 7-17 76 1.3 10 54 76 1.3 PRESENT 7-18 76 1.3 10 54 76 1.3 INVENTION 7-19 76 1.3 10 54 76 1.3 7-20 76 1.3 10 54 76 1.3 7-21 76 1.3 10 54 76 1.3 COMPARATIVE 7-22 13 13 10 125 13 13 EXAMPLE EXAMPLE 7-23 30 11 10 136 30 11 OF 7-24 32 8 10 136 32 8 PRESENT 7-25 32 8 10 136 32 8 INVENTION 7-26 32 8 10 136 32 8 7-27 32 8 10 136 32 8 7-28 32 8 10 136 32 8 COMPARATIVE 7-29 13 13 10 125 13 13 EXAMPLE EXAMPLE 7-30 43 45 10 135 43 4.5 OF 7-31 53 2.4 10 136 53 2.4 PRESENT 7-32 53 2.4 10 136 53 2.4 INVENTION 7-33 53 2.4 10 136 53 2.4 7-34 53 2.4 10 136 53 2.4 7-35 53 2.4 10 136 53 2.4 COMPARATIVE 7-36 13 13 10 125 13 13 EXAMPLE EXAMPLE 7-37 59 3.5 10 136 59 3.5 OF 7-38 70 0.4 10 136 70 0.4 PRESENT 7-39 70 0.4 10 136 70 0.4 INVENTION 7-40 70 0.4 10 136 70 0.4 7-41 70 0.4 10 136 70 0.4 7-42 70 0.4 10 136 70 0.4

Further, an alloying ratio of the metal layer and a ratio of an α single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass % or less and the content of ferrite former was 99.5 mass % or more was regarded as an alloy layer. Further, a region where the Mo content was 3.8 mass % or more was regarded as the α single phase region, and a ratio of the α single phase region was found from the aforesaid expression (4). Results of these are listed in Table 19.

Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss W10/1k (W10/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 19.

TABLE 19 RATIO OF ACCUMULATION ACCUMULATION ALLOYING α SINGLE DEGREE OF DEGREE OF CONDITION RATE PHASE {200} PLANE {222} PLANE B50 Bs B50/ W10/1k No. (%) (%) (%) (%) (T) (T) Bs (W/kg) COMPARATIVE 7-1 0 0 13 13 1.60 2.05 0.78 91 EXAMPLE EXAMPLE 7-2 8 0.2 30 10 1.74 2.05 0.85 62 OF 7-3 82 1.5 31 10 1.74 2.05 0.85 57 PRESENT 7-4 95 8.2 30 10 1.74 2.05 0.85 44 INVENTION 7-5 100 35 30 10 1.74 2.05 0.85 37 7-6 100 73 30 10 1.74 2.05 0.85 43 7-7 100 87 30 10 1.74 2.05 0.85 58 COMPARATIVE 7-8 0 0 13 13 1.60 2.05 0.78 93 EXAMPLE EXAMPLE 7-9 7 0.2 41 5.8 1.78 2.05 0.87 63 OF 7-10 64 2.6 53 2.7 1.85 2.05 0.90 57 PRESENT 7-11 94 7.8 53 2.7 1.87 2.05 0.91 42 INVENTION 7-12 100 42 53 2.7 1.85 2.05 0.90 33 7-13 100 71 53 2.7 1.85 2.05 0.90 38 7-14 100 95 53 2.7 1.87 2.05 0.91 53 COMPARATIVE 7-15 0 0 13 13 1.62 2.05 0.79 93 EXAMPLE EXAMPLE 7-16 7 0.3 60 2.5 1.91 2.05 0.93 61 OF 7-17 67 1.2 75 1.3 1.95 2.05 0.95 48 PRESENT 7-18 89 5.9 75 1.4 1.93 2.05 0.94 41 INVENTION 7-19 100 37 75 1.3 1.95 2.05 0.95 28 7-20 100 72 76 1.4 1.97 2.05 0.96 33 7-21 100 87 75 1.7 1.95 2.05 0.95 48 COMPARATIVE 7-22 0 0 13 13 1.60 2.05 0.78 98 EXAMPLE EXAMPLE 7-23 4 0.2 30 11 1.74 2.05 0.85 64 OF 7-24 57 1.2 32 9 1.74 2.05 0.85 56 PRESENT 7-25 87 6.7 32 9 1.74 2.05 0.85 45 INVENTION 7-26 100 45 32 9 1.74 2.05 0.85 37 7-27 100 72 32 9 1.74 2.05 0.85 42 7-28 100 92 32 9 1.74 2.05 0.85 57 COMPARATIVE 7-29 0 0 13 13 1.60 2.05 0.78 100 EXAMPLE EXAMPLE 7-30 8 0.2 43 4.5 1.78 2.05 0.87 64 OF 7-31 54 1.3 56 2.1 1.87 2.05 0.91 52 PRESENT 7-32 78 6.1 56 2.1 1.85 2.05 0.90 41 INVENTION 7-33 100 38 56 2.2 1.87 2.05 0.91 32 7-34 100 71 56 2.1 1.85 2.05 0.90 38 7-35 100 91 56 2.2 1.87 2.05 0.91 54 COMPARATIVE 7-36 0 0 13 13 1.62 2.05 0.79 97 EXAMPLE EXAMPLE 7-37 6 0.1 59 3.5 1.91 2.05 0.93 62 OF 7-38 70 2.3 82 0.8 1.95 2.05 0.95 46 PRESENT 7-39 91 7.1 82 0.8 1.95 2.05 0.95 40 INVENTION 7-40 100 41 82 0.8 1.97 2.05 0.96 26 7-41 100 76 82 0.8 1.95 2.05 0.95 32 7-42 100 100 82 0.8 1.97 2.05 0.96 48

As listed in Table 18, in examples of the present invention (conditions No. 7-2 to No. 7-7, No. 7-9 to No. 7-14, No. 7-16 to No. 7-21, No. 7-23 to No. 7-28, No. 7-30 to No. 7-35, No. 7-37 to No. 7-42), the accumulation degree of the {200} planes in the α phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 19, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were within the desirable ranges of the present invention. As listed in Table 19, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the α phase was 30% or more and the accumulation degree of the {222} planes in the α phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more.

In the examples of the present invention, when the ratio of the α single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss W10/1k maintained a higher property level. Further, it could be confirmed that the core loss W10/1k has a still better property level when the ratio of the α single phase region is not less than 5% nor more than 80%.

Eighth Experiment

In an eighth experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. 8-1 to condition No. 8-42) were studied.

Base metal plates (silicon steel plates) used in the eighth experiment contained components of the composition R listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the eighth experiment transformed to a γ single phase was 1010° C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 8-1 to the condition No. 8-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively.

Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 μm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 20.

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the α phase was within a 17% to 24% range in each of the base metal plates.

Thereafter, V layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by an sputtering method, except in the conditions No. 8-1, No. 8-8, No. 8-15, No. 8-22, No. 8-29, and No. 8-36. Thickness of each of the V layers (total thickness on the both surfaces) is listed in Table 20.

Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 20.

TABLE 20 FIRST SAMPLE BASE METAL PLATE ACCUMULATION REDUCTION DISLOCATION METAL LAYER HETING MEASURED DEGREE OF CONDITION RATE DENSITY THICKNESS THICKNESS RATE TEMPERATURE {200} PLANE No. COMPOSITION BLASTING (%) (m/m³) (μm) ELEMENT (μm) (° C./s) (° C.) (%) COMPARATIVE 8-1 R WITHOUT 95 1 × 10¹⁵ 100 NONE 50 1010 17 EXAMPLE EXAMPLE 8-2 R WITHOUT 95 1 × 10¹⁵ 100 V 4 50 1010 25 OF 8-3 R WITHOUT 95 1 × 10¹⁵ 100 V 4 50 1010 25 PRESENT 8-4 R WITHOUT 95 1 × 10¹⁵ 100 V 4 50 1010 25 INVENTION 8-5 R WITHOUT 95 1 × 10¹⁵ 100 V 4 50 1010 25 8-6 R WITHOUT 95 1 × 10¹⁵ 100 V 4 50 1010 25 8-7 R WITHOUT 95 1 × 10¹⁵ 100 V 4 50 1010 25 COMPARATIVE 8-8 R WITHOUT 97.5 1 × 10¹⁶ 100 NONE 50 1010 17 EXAMPLE EXAMPLE 8-9 R WITHOUT 97.5 1 × 10¹⁶ 100 V 4 50 1010 31 OF 8-10 R WITHOUT 97.5 1 × 10¹⁶ 100 V 4 50 1010 31 PRESENT 8-11 R WITHOUT 97.5 1 × 10¹⁶ 100 V 4 50 1010 31 INVENTION 8-12 R WITHOUT 97.5 1 × 10¹⁶ 100 V 4 50 1010 31 8-13 R WITHOUT 97.5 1 × 10¹⁶ 100 V 4 50 1010 31 8-14 R WITHOUT 97.5 1 × 10¹⁶ 100 V 4 50 1010 31 COMPARATIVE 8-15 R WITH 95 8 × 10¹⁶ 100 NONE 50 1010 17 EXAMPLE EXAMPLE 8-16 R WITH 95 8 × 10¹⁶ 100 V 4 50 1010 48 OF 8-17 R WITH 95 8 × 10¹⁶ 100 V 4 50 1010 48 PRESENT 8-18 R WITH 95 8 × 10¹⁶ 100 V 4 50 1010 48 INVENTION 8-19 R WITH 95 8 × 10¹⁶ 100 V 4 50 1010 48 8-20 R WITH 95 8 × 10¹⁶ 100 V 4 50 1010 48 8-21 R WITH 95 8 × 10¹⁶ 100 V 4 50 1010 48 COMPARATIVE 8-22 R WITHOUT 95 1 × 10¹⁵ 250 NONE 50 1010 17 EXAMPLE EXAMPLE 8-23 R WITHOUT 95 1 × 10¹⁵ 250 V 10 50 1010 27 OF 8-24 R WITHOUT 95 1 × 10¹⁵ 250 V 10 50 1010 27 PRESENT 8-25 R WITHOUT 95 1 × 10¹⁵ 250 V 10 50 1010 27 INVENTION 8-26 R WITHOUT 95 1 × 10¹⁵ 250 V 10 50 1010 27 8-27 R WITHOUT 95 1 × 10¹⁵ 250 V 10 50 1010 27 8-28 R WITHOUT 95 1 × 10¹⁵ 250 V 10 50 1010 27 COMPARATIVE 8-29 R WITHOUT 97.5 1 × 10¹⁶ 250 NONE 50 1010 18 EXAMPLE EXAMPLE 8-30 R WITHOUT 97.5 1 × 10¹⁶ 250 V 10 50 1010 33 OF 8-31 R WITHOUT 97.5 1 × 10¹⁶ 250 V 10 50 1010 33 PRESENT 8-32 R WITHOUT 97.5 1 × 10¹⁶ 250 V 10 50 1010 33 INVENTION 8-33 R WITHOUT 97.5 1 × 10¹⁶ 250 V 10 50 1010 33 8-34 R WITHOUT 97.5 1 × 10¹⁶ 250 V 10 50 1010 33 8-35 R WITHOUT 97.5 1 × 10¹⁶ 250 V 10 50 1010 33 COMPARATIVE 8-36 R WITH 95 8 × 10¹⁶ 250 NONE 50 1010 17 EXAMPLE EXAMPLE 8-37 R WITH 95 8 × 10¹⁶ 250 V 10 50 1010 53 OF 8-38 R WITH 95 8 × 10¹⁶ 250 V 10 50 1010 53 PRESENT 8-39 R WITH 95 8 × 10¹⁶ 250 V 10 50 1010 53 INVENTION 8-40 R WITH 95 8 × 10¹⁶ 250 V 10 50 1010 53 8-41 R WITH 95 8 × 10¹⁶ 250 V 10 50 1010 53 8-42 R WITH 95 8 × 10¹⁶ 250 V 10 50 1010 53 FIRST SAMPLE SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION ACCUMULATION ACCUMULATION ACCUMULATION DEGREE OF KEEPING KEEPING DEGREE OF DEGREE OF COOLING DEGREE OF DEGREE OF CONDITION {222} PLANE TEMPERATURE TIME {200} PLANE {222} PLANE RATE DISTANCE {200} PLANE {222} PLANE No. (%) (° C.) (s) (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 8-1 13 1050 2 13 13 10 50 13 13 EXAMPLE EXAMPLE 8-2 16 1010 2 30 12 10 54 30 12 OF 8-3 16 1050 2 32 8 10 54 32 8 PRESENT 8-4 16 1050 5 32 8 10 54 32 8 INVENTION 8-5 16 1050 30 32 8 10 54 32 8 8-6 16 1050 120 32 8 10 54 32 8 8-7 16 1050 360 32 8 10 54 32 8 COMPARATIVE 8-8 12 1050 2 13 13 10 50 13 13 EXAMPLE EXAMPLE 8-9 6 1010 2 42 5.8 10 54 42 5.8 OF 8-10 6 1050 2 51 2.8 10 54 51 2.8 PRESENT 8-11 6 1050 5 51 2.8 10 54 51 2.8 INVENTION 8-12 6 1050 30 51 2.8 10 54 51 2.8 8-13 6 1050 120 51 2.8 10 54 51 2.8 8-14 6 1050 360 51 2.8 10 54 51 2.8 COMPARATIVE 8-15 12 1050 2 13 13 10 50 13 13 EXAMPLE EXAMPLE 8-16 4.8 1010 2 59 3.1 10 54 59 3.1 OF 8-17 4.8 1050 2 73 1.6 10 54 73 1.6 PRESENT 8-18 4.8 1050 5 73 1.6 10 54 73 1.6 INVENTION 8-19 4.8 1050 30 73 1.6 10 54 73 1.6 8-20 4.8 1050 120 73 1.6 10 54 73 1.6 8-21 4.8 1050 360 73 1.6 10 54 73 1.6 COMPARATIVE 8-22 13 1100 2 13 13 10 125 13 13 EXAMPLE EXAMPLE 8-23 11 1010 2 30 11 10 136 30 11 OF 8-24 11 1100 3 31 10 10 136 31 10 PRESENT 8-25 11 1100 7 31 10 10 136 31 10 INVENTION 8-26 11 1100 35 31 10 10 136 31 10 8-27 11 1100 140 31 10 10 136 31 10 8-28 11 1100 420 31 10 10 136 31 10 COMPARATIVE 8-29 13 1100 2 13 13 10 125 13 13 EXAMPLE EXAMPLE 8-30 7 1010 2 43 5.1 10 136 43 5.1 OF 8-31 7 1100 3 58 1.7 10 136 58 1.7 PRESENT 8-32 7 1100 7 58 1.7 10 136 58 1.7 INVENTION 8-33 7 1100 35 58 1.7 10 136 58 1.7 8-34 7 1100 140 58 1.7 10 136 58 1.7 8-35 7 1100 420 58 1.7 10 136 58 1.7 COMPARATIVE 8-36 12 1100 2 13 13 10 125 13 13 EXAMPLE EXAMPLE 8-37 3.9 1010 2 62 2.1 10 136 62 2.1 OF 8-38 3.9 1100 3 76 0.5 10 136 76 0.5 PRESENT 8-39 3.9 1100 7 76 0.5 10 136 76 0.5 INVENTION 8-40 3.9 1100 35 76 0.5 10 136 76 0.5 8-41 3.9 1100 140 76 0.5 10 136 76 0.5 8-42 3.9 1100 420 76 0.5 10 136 76 0.5

Further, an alloying ratio of the metal layer and a ratio of an α single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass % or less and the content of ferrite former was 99.5 mass % or more was regarded as an alloy layer. Further, a region where the V content was 1.8 mass % or more was regarded as the α single phase region, and a ratio of the α single phase region was found from the aforesaid expression (4). Results of these are listed in Table 21.

Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss W10/1k (W10/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 21.

TABLE 21 RATIO OF ACCUMULATION ACCUMULATION ALLOYING α SINGLE DEGREE OF DEGREE OF CONDITION RATE PHASE {200} PLANE {222} PLANE B50 Bs B50/ W10/1k No. (%) (%) (%) (%) (T) (T) Bs (W/kg) COMPARATIVE 8-1 0 0 13 13 1.60 2.05 0.78 91 EXAMPLE EXAMPLE 8-2 8 0.2 30 12 1.74 2.05 0.85 62 OF 8-3 82 1.5 31 10 1.74 2.05 0.85 57 PRESENT 8-4 95 8.2 30 10 1.74 2.05 0.85 44 INVENTION 8-5 100 35 30 10 1.74 2.05 0.85 37 8-6 100 73 30 10 1.74 2.05 0.85 43 8-7 100 87 30 10 1.74 2.05 0.85 58 COMPARATIVE 8-8 0 0 13 13 1.60 2.05 0.78 93 EXAMPLE EXAMPLE 8-9 6 0.2 42 5.8 1.76 2.05 0.86 61 OF 8-10 64 2.6 53 2.7 1.85 2.05 0.90 57 PRESENT 8-11 94 7.8 53 2.7 1.87 2.05 0.91 42 INVENTION 8-12 100 42 53 2.7 1.85 2.05 0.90 33 8-13 100 71 53 2.7 1.85 2.05 0.90 38 8-14 100 95 53 2.7 1.87 2.05 0.91 53 COMPARATIVE 8-15 0 0 13 13 1.62 2.05 0.79 94 EXAMPLE EXAMPLE 8-16 7 0.3 59 3.1 1.89 2.05 0.92 62 OF 8-17 67 1.2 75 1.3 1.95 2.05 0.95 48 PRESENT 8-18 89 5.9 75 1.4 1.93 2.05 0.94 41 INVENTION 8-19 100 37 75 1.3 1.95 2.05 0.95 28 8-20 100 72 76 1.4 1.97 2.05 0.96 33 8-21 100 87 75 1.7 1.95 2.05 0.95 48 COMPARATIVE 8-22 0 0 13 13 1.60 2.05 0.78 103 EXAMPLE EXAMPLE 8-23 5 0.1 30 11 1.74 2.05 0.85 63 OF 8-24 57 1.2 32 9 1.74 2.05 0.85 56 PRESENT 8-25 87 6.7 32 9 1.74 2.05 0.85 45 INVENTION 8-26 100 45 32 9 1.74 2.05 0.85 37 8-27 100 74 32 9 1.74 2.05 0.85 42 8-28 100 92 32 9 1.74 2.05 0.85 57 COMPARATIVE 8-29 0 0 13 13 1.60 2.05 0.78 102 EXAMPLE EXAMPLE 8-30 8 0.3 43 5.1 1.78 2.05 0.87 63 OF 8-31 54 1.3 56 2.1 1.87 2.05 0.91 52 PRESENT 8-32 78 6.1 56 2.1 1.85 2.05 0.90 41 INVENTION 8-33 100 38 56 2.2 1.87 2.05 0.91 32 8-34 100 71 56 2.1 1.85 2.05 0.90 38 8-35 100 91 56 2.2 1.87 2.05 0.91 54 COMPARATIVE 8-36 0 0 13 13 1.62 2.05 0.79 99 EXAMPLE EXAMPLE 8-37 5 0.1 62 2.1 1.89 2.05 0.92 62 OF 8-38 70 2.3 82 0.8 1.95 2.05 0.95 46 PRESENT 8-39 91 7.1 82 0.8 1.95 2.05 0.95 40 INVENTION 8-40 100 41 82 0.8 1.97 2.05 0.96 26 8-41 100 76 82 0.8 1.95 2.05 0.95 32 8-42 100 100 82 0.8 1.97 2.05 0.96 48

As listed in Table 20, in examples of the present invention (conditions No. 8-2 to No. 8-7, No. 8-9 to No. 8-14, No. 8-16 to No. 8-21, No. 8-23 to No. 8-28, No. 8-30 to No. 8-35, No. 8-37 to No. 8-42), the accumulation degree of the {200} planes in the α phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 21, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were within the desirable ranges of the present invention. As listed in Table 21, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the α phase was 30% or more and the accumulation degree of the {222} planes in the α phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more.

In the examples of the present invention, when the ratio of the α single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss W10/1k maintained a higher property level. Further, it could be confirmed that the core loss W10/1k has a still better property level when the ratio of the α single phase region is not less than 5% nor more than 80%.

Ninth Experiment

In a ninth experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. 9-1 to condition No. 9-42) were studied.

Base metal plates (silicon steel plates) used in the ninth experiment contained components of the composition S listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the ninth experiment transformed to a γ single phase was 1080° C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 9-1 to the condition No. 9-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively.

Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 μm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 22.

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the α phase was within a 17% to 24% range in each of the base metal plates.

Thereafter, Cr layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by an electroplating method, except in the conditions No. 9-1, No. 9-8, No. 9-15, No. 9-22, No. 9-29, and No. 9-36. Thickness of each of the Cr layers (total thickness on the both surfaces) is listed in Table 22.

Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 22.

TABLE 22 FIRST SAMPLE BASE METAL PLATE ACCUMULATION REDUCTION DISLOCATION METAL LAYER HETING MEASURED DEGREE OF CONDITION RATE DENSITY THICKNESS THICKNESS RATE TEMPERATURE {200} PLANE No. COMPOSITION BLASTING (%) (m/m³) (μm) ELEMENT (μm) (° C./s) (° C.) (%) COMPARATIVE 9-1 S WITHOUT 95 1 × 10¹⁵ 100 NONE 50 1080 16 EXAMPLE EXAMPLE 9-2 S WITHOUT 95 1 × 10¹⁵ 100 Cr 3 50 1080 27 OF 9-3 S WITHOUT 95 1 × 10¹⁵ 100 Cr 3 50 1080 27 PRESENT 9-4 S WITHOUT 95 1 × 10¹⁵ 100 Cr 3 50 1080 27 INVENTION 9-5 S WITHOUT 95 1 × 10¹⁶ 100 Cr 3 50 1080 27 9-6 S WITHOUT 95 1 × 10¹⁵ 100 Cr 3 50 1080 27 9-7 S WITHOUT 95 1 × 10¹⁵ 100 Cr 3 50 1080 27 COMPARATIVE 9-8 S WITHOUT 97.5 1 × 10¹⁶ 100 NONE 50 1080 16 EXAMPLE EXAMPLE 9-9 S WITHOUT 97.5 1 × 10¹⁶ 100 Cr 3 50 1080 32 OF 9-10 S WITHOUT 97.5 1 × 10¹⁶ 100 Cr 3 50 1080 32 PRESENT 9-11 S WITHOUT 97.5 1 × 10¹⁶ 100 Cr 3 50 1080 32 INVENTION 9-12 S WITHOUT 97.5 1 × 10¹⁶ 100 Cr 3 50 1080 32 9-13 S WITHOUT 97.5 1 × 10¹⁶ 100 Cr 3 50 1080 32 9-14 S WITHOUT 97.5 1 × 10¹⁶ 100 Cr 3 50 1080 32 COMPARATIVE 9-15 S WITH 95 8 × 10¹⁶ 100 NONE 50 1080 16 EXAMPLE EXAMPLE 9-16 S WITH 95 8 × 10¹⁶ 100 Cr 3 50 1080 58 OF 9-17 S WITH 95 8 × 10¹⁶ 100 Cr 3 50 1080 58 PRESENT 9-18 S WITH 95 8 × 10¹⁶ 100 Cr 3 50 1080 58 INVENTION 9-19 S WITH 95 8 × 10¹⁶ 100 Cr 3 50 1080 58 9-20 S WITH 95 8 × 10¹⁶ 100 Cr 3 50 1080 58 9-21 S WITH 95 8 × 10¹⁶ 100 Cr 3 50 1080 58 COMPARATIVE 9-22 S WITHOUT 95 1 × 10¹⁵ 250 NONE 50 1080 16 EXAMPLE EXAMPLE 9-23 S WITHOUT 95 1 × 10¹⁵ 250 Cr 8 50 1080 25 OF 9-24 S WITHOUT 95 1 × 10¹⁵ 250 Cr 8 50 1080 25 PRESENT 9-25 S WITHOUT 95 1 × 10¹⁶ 250 Cr 8 50 1080 25 INVENTION 9-26 S WITHOUT 95 1 × 10¹⁵ 250 Cr 8 50 1080 25 9-27 S WITHOUT 95 1 × 10¹⁵ 250 Cr 8 50 1080 25 9-28 S WITHOUT 95 1 × 10¹⁵ 250 Cr 8 50 1080 25 COMPARATIVE 9-29 S WITHOUT 97.5 1 × 10¹⁶ 250 NONE 50 1080 16 EXAMPLE EXAMPLE 9-30 S WITHOUT 97.5 1 × 10¹⁶ 250 Cr 8 50 1080 35 OF 9-31 S WITHOUT 97.5 1 × 10¹⁶ 250 Cr 8 50 1080 35 PRESENT 9-32 S WITHOUT 97.5 1 × 10¹⁶ 250 Cr 8 50 1080 35 INVENTION 9-33 S WITHOUT 97.5 1 × 10¹⁶ 250 Cr 8 50 1080 35 9-34 S WITHOUT 97.5 1 × 10¹⁶ 250 Cr 8 50 1080 35 9-35 S WITHOUT 97.5 1 × 10¹⁶ 250 Cr 8 50 1080 35 COMPARATIVE 9-36 S WITH 95 8 × 10¹⁶ 250 NONE 50 1080 16 EXAMPLE EXAMPLE 9-37 S WITH 95 8 × 10¹⁶ 250 Cr 8 50 1080 52 OF 9-38 S WITH 95 8 × 10¹⁶ 250 Cr 8 50 1080 52 PRESENT 9-39 S WITH 95 8 × 10¹⁶ 250 Cr 8 50 1080 52 INVENTION 9-40 S WITH 95 8 × 10¹⁶ 250 Cr 8 50 1080 52 9-41 S WITH 95 8 × 10¹⁶ 250 Cr 8 50 1080 52 9-42 S WITH 95 8 × 10¹⁶ 250 Cr 8 50 1080 52 FIRST SAMPLE SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION ACCUMULATION ACCUMULATION ACCUMULATION DEGREE OF KEEPING KEEPING DEGREE OF DEGREE OF COOLING DEGREE OF DEGREE OF CONDITION {222} PLANE TEMPERATURE TIME {200} PLANE {222} PLANE RATE DISTANCE {200} PLANE {222} PLANE No. (%) (° C.) (s) (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 9-1 13 1080 2 13 13 50 50 13 13 EXAMPLE EXAMPLE 9-2 13 1080 2 30 10 50 54 30 10 OF 9-3 13 1130 2 30 11 50 54 30 11 PRESENT 9-4 13 1130 5 30 11 50 54 30 11 INVENTION 9-5 13 1130 30 30 11 50 54 30 11 9-6 13 1130 120 30 11 50 54 30 11 9-7 13 1130 360 30 11 50 54 30 11 COMPARATIVE 9-8 13 1130 2 13 13 50 50 13 13 EXAMPLE EXAMPLE 9-9 5 1080 2 46 4.8 50 54 46 4.8 OF 9-10 5 1130 2 57 2.1 50 54 57 2.1 PRESENT 9-11 5 1130 5 57 2.1 50 54 57 2.1 INVENTION 9-12 5 1130 30 57 2.1 50 54 57 2.1 9-13 5 1130 120 57 2.1 50 54 57 2.1 9-14 5 1130 360 57 2.1 50 54 57 2.1 COMPARATIVE 9-15 13 1130 2 13 13 50 50 13 13 EXAMPLE EXAMPLE 9-16 3.1 1080 2 61 2.3 50 54 61 2.3 OF 9-17 3.1 1130 2 81 0.8 50 54 81 0.8 PRESENT 9-18 3.1 1130 5 81 0.8 50 54 81 0.8 INVENTION 9-19 3.1 1130 30 81 0.8 50 54 81 0.8 9-20 3.1 1130 120 81 0.8 50 54 81 0.8 9-21 3.1 1130 360 81 0.8 50 54 81 0.8 COMPARATIVE 9-22 13 1180 2 13 13 50 125 13 13 EXAMPLE EXAMPLE 9-23 12 1080 2 30 12 50 136 30 12 OF 9-24 12 1180 3 33 7 50 136 33 7 PRESENT 9-25 12 1180 7 33 7 50 136 33 7 INVENTION 9-26 12 1180 35 33 7 50 136 33 7 9-27 12 1180 140 33 7 50 136 33 7 9-28 12 1180 420 33 7 50 136 33 7 COMPARATIVE 9-29 13 1180 2 13 13 50 125 13 13 EXAMPLE EXAMPLE 9-30 6 1080 2 42 5.2 50 136 42 5.2 OF 9-31 6 1180 3 53 2.3 50 136 53 2.3 PRESENT 9-32 6 1180 7 53 2.3 50 136 53 2.3 INVENTION 9-33 6 1180 35 53 2.3 50 136 53 2.3 9-34 6 1180 140 53 2.3 50 136 53 2.3 9-35 6 1180 420 53 2.3 50 136 53 2.3 COMPARATIVE 9-36 13 1180 2 13 13 50 125 13 13 EXAMPLE EXAMPLE 9-37 4.2 1080 2 62 2 50 136 62 2 OF 9-38 4.2 1180 3 74 0.9 50 136 74 0.9 PRESENT 9-39 4.2 1180 7 74 0.9 50 136 74 0.9 INVENTION 9-40 4.2 1180 35 74 0.9 50 136 74 0.9 9-41 4.2 1180 140 74 0.9 50 136 74 0.9 9-42 4.2 1180 420 74 0.9 50 136 74 0.9

Further, an alloying ratio of the metal layer and a ratio of an α single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass % or less and the content of ferrite former was 99.5 mass % or more was regarded as an alloy layer. Further, a region where the Cr content was 13.0 mass % or more was regarded as the α single phase region, and a ratio of the α single phase region was found from the aforesaid expression (4). Results of these are listed in Table 23.

Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss W10/1k (W10/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 23.

TABLE 23 RATIO OF ACCUMULATION ACCUMULATION ALLOYING α SINGLE DEGREE OF DEGREE OF CONDITION RATE PHASE {200} PLANE {222} PLANE B50 Bs B50/ W10/1k No. (%) (%) (%) (%) (T) (T) Bs (W/kg) COMPARATIVE 9-1 0 0 13 13 1.60 2.05 0.78 95 EXAMPLE EXAMPLE 9-2 6 0.2 30 10 1.74 2.05 0.85 62 OF 9-3 82 1.5 31 10 1.74 2.05 0.85 57 PRESENT 9-4 95 8.2 30 10 1.74 2.05 0.85 44 INVENTION 9-5 100 35 30 10 1.74 2.05 0.85 37 9-6 100 73 30 10 1.74 2.05 0.85 43 9-7 100 87 30 10 1.74 2.05 0.85 58 COMPARATIVE 9-8 0 0 13 13 1.60 2.05 0.78 93 EXAMPLE EXAMPLE 9-9 10 0.4 46 4.8 1.78 2.05 0.87 61 OF 9-10 64 2.6 53 2.7 1.85 2.05 0.90 57 PRESENT 9-11 94 7.8 53 2.7 1.87 2.05 0.91 42 INVENTION 9-12 100 42 53 2.7 1.85 2.05 0.90 33 9-13 100 71 53 2.7 1.85 2.05 0.90 38 9-14 100 95 53 2.7 1.87 2.05 0.91 53 COMPARATIVE 9-15 0 0 13 13 1.62 2.05 0.79 94 EXAMPLE EXAMPLE 9-16 9 0.3 61 2.3 1.89 2.05 0.92 62 OF 9-17 67 1.2 75 1.3 1.95 2.05 0.95 48 PRESENT 9-18 89 5.9 75 1.4 1.93 2.05 0.94 41 INVENTION 9-19 100 37 75 1.3 1.95 2.05 0.95 28 9-20 100 72 76 1.4 1.97 2.05 0.96 33 9-21 100 87 75 1.7 1.95 2.05 0.95 48 COMPARATIVE 9-22 0 0 13 13 1.60 2.05 0.78 98 EXAMPLE EXAMPLE 9-23 6 0.2 30 12 1.74 2.05 0.85 65 OF 9-24 57 1.2 32 9 1.74 2.05 0.85 56 PRESENT 9-25 87 6.7 32 9 1.74 2.05 0.85 45 INVENTION 9-26 100 45 32 9 1.74 2.05 0.85 37 9-27 100 72 32 9 1.74 2.05 0.85 42 9-28 100 92 32 9 1.74 2.05 0.85 57 COMPARATIVE 9-29 0 0 13 13 1.60 2.05 0.78 96 EXAMPLE EXAMPLE 9-30 5 0.1 42 5.2 1.78 2.05 0.87 64 OF 9-31 54 1.3 56 2.1 1.87 2.05 0.91 52 PRESENT 9-32 78 6.1 56 2.1 1.85 2.05 0.90 41 INVENTION 9-33 100 38 56 2.2 1.87 2.05 0.91 32 9-34 100 71 56 2.1 1.85 2.05 0.90 38 9-35 100 91 56 2.2 1.87 2.05 0.91 54 COMPARATIVE 9-36 0 0 13 13 1.62 2.05 0.79 100 EXAMPLE EXAMPLE 9-37 5 0.1 62 2 1.89 2.05 0.92 64 OF 9-38 70 2.3 82 0.8 1.95 2.05 0.95 46 PRESENT 9-39 91 7.1 82 0.8 1.95 2.05 0.95 40 INVENTION 9-40 100 41 82 0.8 1.97 2.05 0.96 26 9-41 100 76 82 0.8 1.95 2.05 0.95 32 9-42 100 100 82 0.8 1.97 2.05 0.96 48

As listed in Table 22, in examples of the present invention (conditions No. 9-2 to No. 9-7, No. 9-9 to No. 9-14, No. 9-16 to No. 9-21, No. 9-23 to No. 9-28, No. 9-30 to No. 9-35, No. 9-37 to No. 9-42), the accumulation degree of the {200} planes in the α phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 23, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were within the desirable ranges of the present invention. As listed in Table 23, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the α phase was 30% or more and the accumulation degree of the {222} planes in the α phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more.

In the examples of the present invention, when the ratio of the α single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss W10/1 k maintained a higher property level. Further, it could be confirmed that the core loss W10/1 k has a still better property level when the ratio of the α single phase region is not less than 5% nor more than 80%.

Tenth Experiment

In a tenth experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. 10-1 to condition No. 10-42) were studied.

Base metal plates (silicon steel plates) used in the tenth experiment contained components of the composition T listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the tenth experiment transformed to a γ single phase was 1020° C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 10-1 to the condition No. 10-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively.

Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 μm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 24.

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the α phase was within a 17% to 24% range in each of the base metal plates.

Thereafter, Ti layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by a sputtering method, except in the conditions No. 10-1, No. 10-8, No. 10-15, No. 10-22, No. 10-29, and No. 10-36. Thickness of each of the Ti layers (total thickness on the both surfaces) is listed in Table 24.

Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes of the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 24.

TABLE 24 FIRST SAMPLE BASE METAL PLATE ACCUMULATION REDUCTION DISLOCATION METAL LAYER HETING MEASURED DEGREE OF CONDITION RATE DENSITY THICKNESS THICKNESS RATE TEMPERATURE {200} PLANE No. COMPOSITION BLASTING (%) (m/m³) (μm) ELEMENT (μm) (° C./s) (° C.) (%) COMPARATIVE 10-1 T WITHOUT 95 1 × 10¹⁵ 100 NONE 50 1020 17 EXAMPLE EXAMPLE 10-2 T WITHOUT 95 1 × 10¹⁵ 100 Ti 5 50 1020 25 OF 10-3 T WITHOUT 95 1 × 10¹⁵ 100 Ti 5 50 1020 25 PRESENT 10-4 T WITHOUT 95 1 × 10¹⁵ 100 Ti 5 50 1020 25 INVENTION 10-5 T WITHOUT 95 1 × 10¹⁵ 100 Ti 5 50 1020 25 10-6 T WITHOUT 95 1 × 10¹⁵ 100 Ti 5 50 1020 25 10-7 T WITHOUT 95 1 × 10¹⁵ 100 Ti 5 50 1020 25 COMPARATIVE 10-8 T WITHOUT 97.5 1 × 10¹⁶ 100 NONE 50 1020 17 EXAMPLE EXAMPLE 10-9 T WITHOUT 97.5 1 × 10¹⁶ 100 Ti 5 50 1020 35 OF 10-10 T WITHOUT 97.5 1 × 10¹⁶ 100 Ti 5 50 1020 35 PRESENT 10-11 T WITHOUT 97.5 1 × 10¹⁶ 100 Ti 5 50 1020 35 INVENTION 10-12 T WITHOUT 97.5 1 × 10¹⁶ 100 Ti 5 50 1020 35 10-13 T WITHOUT 97.5 1 × 10¹⁶ 100 Ti 5 50 1020 35 10-14 T WITHOUT 97.5 1 × 10¹⁶ 100 Ti 5 50 1020 35 COMPARATIVE 10-15 T WITH 95 8 × 10¹⁶ 100 NONE 50 1020 16 EXAMPLE EXAMPLE 10-16 T WITH 95 8 × 10¹⁶ 100 Ti 5 50 1020 61 OF 10-17 T WITH 95 8 × 10¹⁶ 100 Ti 5 50 1020 61 PRESENT 10-18 T WITH 95 8 × 10¹⁶ 100 Ti 5 50 1020 61 INVENTION 10-19 T WITH 95 8 × 10¹⁶ 100 Ti 5 50 1020 61 10-20 T WITH 95 8 × 10¹⁶ 100 Ti 5 50 1020 61 10-21 T WITH 95 8 × 10¹⁶ 100 Ti 5 50 1020 61 COMPARATIVE 10-22 T WITHOUT 95 1 × 10¹⁵ 250 NONE 50 1020 17 EXAMPLE EXAMPLE 10-23 T WITHOUT 95 1 × 10¹⁵ 250 Ti 13 50 1020 26 OF 10-24 T WITHOUT 95 1 × 10¹⁵ 250 Ti 13 50 1020 26 PRESENT 10-25 T WITHOUT 95 1 × 10¹⁵ 250 Ti 13 50 1020 26 INVENTION 10-26 T WITHOUT 95 1 × 10¹⁵ 250 Ti 13 50 1020 26 10-27 T WITHOUT 95 1 × 10¹⁵ 250 Ti 13 50 1020 26 10-28 T WITHOUT 95 1 × 10¹⁵ 250 Ti 13 50 1020 26 COMPARATIVE 10-29 T WITHOUT 97.5 1 × 10¹⁶ 250 NONE 50 1020 17 EXAMPLE EXAMPLE 10-30 T WITHOUT 97.5 1 × 10¹⁶ 250 Ti 13 50 1020 38 OF 10-31 T WITHOUT 97.5 1 × 10¹⁶ 250 Ti 13 50 1020 38 PRESENT 10-32 T WITHOUT 97.5 1 × 10¹⁶ 250 Ti 13 50 1020 38 INVENTION 10-33 T WITHOUT 97.5 1 × 10¹⁶ 250 Ti 13 50 1020 38 10-34 T WITHOUT 97.5 1 × 10¹⁶ 250 Ti 13 50 1020 38 10-35 T WITHOUT 97.5 1 × 10¹⁶ 250 Ti 13 50 1020 38 COMPARATIVE 10-36 T WITH 95 8 × 10¹⁶ 250 NONE 50 1020 18 EXAMPLE EXAMPLE 10-37 T WITH 95 8 × 10¹⁶ 250 Ti 13 50 1020 58 OF 10-38 T WITH 95 8 × 10¹⁶ 250 Ti 13 50 1020 58 PRESENT 10-39 T WITH 95 8 × 10¹⁶ 250 Ti 13 50 1020 58 INVENTION 10-40 T WITH 95 8 × 10¹⁶ 250 Ti 13 50 1020 58 10-41 T WITH 95 8 × 10¹⁶ 250 Ti 13 50 1020 58 10-42 T WITH 95 8 × 10¹⁶ 250 Ti 13 50 1020 58 FIRST SAMPLE SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION ACCUMULATION ACCUMULATION ACCUMULATION DEGREE OF KEEPING KEEPING DEGREE OF DEGREE OF COOLING DEGREE OF DEGREE OF CONDITION {222} PLANE TEMPERATURE TIME {200} PLANE {222} PLANE RATE DISTANCE {200} PLANE {222} PLANE No. (%) (° C.) (s) (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 10-1 13 1050 2 13 13 8 50 13 13 EXAMPLE EXAMPLE 10-2 16 1020 2 30 11 8 54 30 11 OF 10-3 16 1050 2 33 9 8 54 33 9 PRESENT 10-4 16 1050 5 33 9 8 54 33 9 INVENTION 10-5 16 1050 30 33 9 8 54 33 9 10-6 16 1050 120 33 9 8 54 33 9 10-7 16 1050 360 33 9 8 54 33 9 COMPARATIVE 10-8 13 1050 2 13 13 8 50 13 13 EXAMPLE EXAMPLE 10-9 4 1020 2 41 5.8 8 54 41 5.8 OF 10-10 4 1050 2 52 3.2 8 54 52 3.2 PRESENT 10-11 4 1050 5 52 3.2 8 54 52 3.2 INVENTION 10-12 4 1050 30 52 3.2 8 54 52 3.2 10-13 4 1050 120 52 3.2 8 54 52 3.2 10-14 4 1050 360 52 3.2 8 54 52 3.2 COMPARATIVE 10-15 14 1050 2 13 13 8 50 13 13 EXAMPLE EXAMPLE 10-16 2.7 1020 2 64 1.8 8 54 64 1.8 OF 10-17 2.7 1050 2 76 1.2 8 54 76 1.2 PRESENT 10-18 2.7 1050 5 76 1.2 8 54 76 1.2 INVENTION 10-19 2.7 1050 30 76 1.2 8 54 76 1.2 10-20 2.7 1050 120 76 1.2 8 54 76 1.2 10-21 2.7 1050 360 76 1.2 8 54 76 1.2 COMPARATIVE 10-22 14 1100 2 13 13 8 125 13 13 EXAMPLE EXAMPLE 10-23 13 1020 2 30 11 8 136 30 11 OF 10-24 13 1100 3 32 11 8 136 32 11 PRESENT 10-25 13 1100 7 32 11 8 136 32 11 INVENTION 10-26 13 1100 35 32 11 8 136 32 11 10-27 13 1100 140 32 11 8 136 32 11 10-28 13 1100 420 32 11 8 136 32 11 COMPARATIVE 10-29 14 1100 2 13 13 8 125 13 13 EXAMPLE EXAMPLE 10-30 4 1020 2 42 4.2 8 136 42 4.2 OF 10-31 4 1100 3 54 2.9 8 136 54 2.9 PRESENT 10-32 4 1100 7 54 2.9 8 136 54 2.9 INVENTION 10-33 4 1100 35 54 2.9 8 136 54 2.9 10-34 4 1100 140 54 2.9 8 136 54 2.9 10-35 4 1100 420 54 2.9 8 136 54 2.9 COMPARATIVE 10-36 13 1100 2 13 13 8 125 13 13 EXAMPLE EXAMPLE 10-37 3.4 1020 2 63 1.8 8 136 63 1.8 OF 10-38 3.4 1100 3 80 0.7 8 136 80 0.7 PRESENT 10-39 3.4 1100 7 80 0.7 8 136 80 0.7 INVENTION 10-40 3.4 1100 35 80 0.7 8 136 80 0.7 10-41 3.4 1100 140 80 0.7 8 136 80 0.7 10-42 3.4 1100 420 80 0.7 8 136 80 0.7

Further, an alloying ratio of the metal layer and a ratio of an α single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass % or less and the content of ferrite former was 99.5 mass % or more was regarded as an alloy layer. Further, a region where the Ti content was 1.2 mass % or more was regarded as the α single phase region, and a ratio of the α single phase region was found from the aforesaid expression (4). Results of these are listed in Table 25.

Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density 50 to the saturation magnetic flux density Bs was calculated. Further, core loss W10/1 k (W10/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 25.

TABLE 25 RATIO OF ACCUMULATION ACCUMULATION ALLOYING α SINGLE DEGREE OF DEGREE OF CONDITION RATE PHASE {200} PLANE {222} PLANE B50 Bs B50/ W10/1k No. (%) (%) (%) (%) (T) (T) Bs (W/kg) COMPARATIVE 10-1 0 0 13 13 1.60 2.05 0.78 91 EXAMPLE EXAMPLE 10-2 6 0.2 30 11 1.74 2.05 0.85 62 OF 10-3 82 1.5 31 10 1.74 2.05 0.85 57 PRESENT 10-4 95 8.2 30 10 1.74 2.05 0.85 44 INVENTION 10-5 100 35 30 10 1.74 2.05 0.85 37 10-6 100 73 30 10 1.74 2.05 0.85 43 10-7 100 87 30 10 1.74 2.05 0.85 58 COMPARATIVE 10-8 0 0 13 13 1.60 2.05 0.78 93 EXAMPLE EXAMPLE 10-9 8 0.2 41 5.8 1.76 2.05 0.86 62 OF 10-10 64 2.6 53 2.7 1.85 2.05 0.90 57 PRESENT 10-11 94 7.8 53 2.7 1.87 2.05 0.91 42 INVENTION 10-12 100 42 53 2.7 1.85 2.05 0.90 33 10-13 100 71 53 2.7 1.85 2.05 0.90 38 10-14 100 95 53 2.7 1.87 2.05 0.91 53 COMPARATIVE 10-15 0 0 13 13 1.62 2.05 0.79 92 EXAMPLE EXAMPLE 10-16 7 0.3 64 1.8 1.91 2.05 0.93 61 OF 10-17 67 1.2 75 1.3 1.95 2.05 0.95 48 PRESENT 10-18 89 5.9 75 1.4 1.93 2.05 0.94 41 INVENTION 10-19 100 37 75 1.3 1.95 2.05 0.95 28 10-20 100 72 76 1.4 1.97 2.05 0.96 33 10-21 100 87 75 1.7 1.95 2.05 0.95 48 COMPARATIVE 10-22 0 0 13 13 1.60 2.05 0.78 102 EXAMPLE EXAMPLE 10-23 8 0.3 30 11 1.74 2.05 0.85 65 OF 10-24 57 1.2 32 9 1.74 2.05 0.85 56 PRESENT 10-25 87 6.7 32 9 1.74 2.05 0.85 45 INVENTION 10-26 100 45 32 9 1.74 2.05 0.85 37 10-27 100 72 32 9 1.74 2.05 0.85 42 10-28 100 92 32 9 1.74 2.05 0.85 57 COMPARATIVE 10-29 0 0 13 13 1.60 2.05 0.78 99 EXAMPLE EXAMPLE 10-30 5 0.1 42 4.2 1.78 2.05 0.87 65 OF 10-31 54 1.3 56 2.1 1.87 2.05 0.91 52 PRESENT 10-32 78 6.1 56 2.1 1.85 2.05 0.90 41 INVENTION 10-33 100 38 56 2.2 1.87 2.05 0.91 32 10-34 100 71 56 2.1 1.85 2.05 0.90 38 10-35 100 91 56 2.2 1.87 2.05 0.91 54 COMPARATIVE 10-36 0 0 13 13 1.62 2.05 0.79 97 EXAMPLE EXAMPLE 10-37 4 0.1 63 1.8 1.91 2.05 0.93 62 OF 10-38 70 2.3 82 0.8 1.95 2.05 0.95 46 PRESENT 10-39 91 7.1 82 0.8 1.95 2.05 0.95 40 INVENTION 10-40 100 41 82 0.8 1.97 2.05 0.96 26 10-41 100 76 82 0.8 1.95 2.05 0.95 32 10-42 100 100 82 0.8 1.97 2.05 0.96 48

As listed in Table 24, in examples of the present invention (conditions No. 10-2 to No. 10-7, No. 10-9 to No. 10-14, No. 10-16 to No. 10-21, No. 10-23 to No. 10-28, No. 10-30 to No. 10-35, No. 10-37 to No. 10-42), the accumulation degree of the {200} planes in the α phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 25, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were within the desirable ranges of the present invention. As listed in Table 25, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the α phase was 30% or more and the accumulation degree of the {222} planes in the α phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more.

In the examples of the present invention, when the ratio of the α single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss W10/1 k maintained a higher property level. Further, it could be confirmed that the core loss W10/1 k has a still better property level when the ratio of the α single phase region is not less than 5% nor more than 80%.

Eleventh Experiment

In an eleventh experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. 11-1 to condition No. 11-42) were studied.

Base metal plates (silicon steel plates) used in the eleventh experiment contained components of the composition U listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the eleventh experiment transformed to a γ single phase was 1000° C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 11-1 to the condition No. 11-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively.

Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 μm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 26.

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the α phase was within a 17% to 24% range in each of the base metal plates.

Thereafter, Ga layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by a vapor deposition method, except in the conditions No. 11-1, No. 11-8, No. 11-15, No. 11-22, No. 11-29, and No. 11-36. Thickness of each of the Ga layers (total thickness on the both surfaces) is listed in Table 26.

Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 26.

TABLE 26 FIRST SAMPLE BASE METAL PLATE ACCUMULATION REDUCTION DISLOCATION METAL LAYER HETING MEASURED DEGREE OF CONDITION RATE DENSITY THICKNESS THICKNESS RATE TEMPERATURE {200} PLANE No. COMPOSITION BLASTING (%) (m/m³) (μm) ELEMENT (μm) (° C./s) (° C.) (%) COMPARATIVE 11-1 U WITHOUT 95 1 × 10¹⁵ 100 NONE 10 1000 16 EXAMPLE EXAMPLE 11-2 U WITHOUT 95 1 × 10¹⁵ 100 Ge 6 10 1000 25 OF 11-3 U WITHOUT 95 1 × 10¹⁵ 100 Ge 6 10 1000 25 PRESENT 11-4 U WITHOUT 95 1 × 10¹⁵ 100 Ge 6 10 1000 25 INVENTION 11-5 U WITHOUT 95 1 × 10¹⁵ 100 Ge 6 10 1000 25 11-6 U WITHOUT 95 1 × 10¹⁵ 100 Ge 6 10 1000 25 11-7 U WITHOUT 95 1 × 10¹⁵ 100 Ge 6 10 1000 25 COMPARATIVE 11-8 U WITHOUT 97.5 1 × 10¹⁶ 100 NONE 10 1000 16 EXAMPLE EXAMPLE 11-9 U WITHOUT 97.5 1 × 10¹⁶ 100 Ge 6 10 1000 38 OF 11-10 U WITHOUT 97.5 1 × 10¹⁶ 100 Ge 6 10 1000 38 PRESENT 11-11 U WITHOUT 97.5 1 × 10¹⁶ 100 Ge 6 10 1000 38 INVENTION 11-12 U WITHOUT 97.5 1 × 10¹⁶ 100 Ge 6 10 1000 38 11-13 U WITHOUT 97.5 1 × 10¹⁶ 100 Ge 6 10 1000 38 11-14 U WITHOUT 97.5 1 × 10¹⁶ 100 Ge 6 10 1000 38 COMPARATIVE 11-15 U WITH 95 8 × 10¹⁶ 100 NONE 10 1000 17 EXAMPLE EXAMPLE 11-16 U WITH 95 8 × 10¹⁶ 100 Ge 6 10 1000 48 OF 11-17 U WITH 95 8 × 10¹⁶ 100 Ge 6 10 1000 48 PRESENT 11-18 U WITH 95 8 × 10¹⁶ 100 Ge 6 10 1000 48 INVENTION 11-19 U WITH 95 8 × 10¹⁶ 100 Ge 6 10 1000 48 11-20 U WITH 95 8 × 10¹⁶ 100 Ge 6 10 1000 48 11-21 U WITH 95 8 × 10¹⁶ 100 Ge 6 10 1000 48 COMPARATIVE 11-22 U WITHOUT 95 1 × 10¹⁵ 250 NONE 10 1000 17 EXAMPLE EXAMPLE 11-23 U WITHOUT 95 1 × 10¹⁵ 250 Ge 14 10 1000 26 OF 11-24 U WITHOUT 95 1 × 10¹⁵ 250 Ge 14 10 1000 26 PRESENT 11-25 U WITHOUT 95 1 × 10¹⁵ 250 Ge 14 10 1000 26 INVENTION 11-26 U WITHOUT 95 1 × 10¹⁵ 250 Ge 14 10 1000 26 11-27 U WITHOUT 95 1 × 10¹⁵ 250 Ge 14 10 1000 26 11-28 U WITHOUT 95 1 × 10¹⁵ 250 Ge 14 10 1000 26 COMPARATIVE 11-29 U WITHOUT 97.5 1 × 10¹⁶ 250 NONE 10 1000 17 EXAMPLE EXAMPLE 11-30 U WITHOUT 97.5 1 × 10¹⁶ 250 Ge 14 10 1000 35 OF 11-31 U WITHOUT 97.5 1 × 10¹⁶ 250 Ge 14 10 1000 35 PRESENT 11-32 U WITHOUT 97.5 1 × 10¹⁶ 250 Ge 14 10 1000 35 INVENTION 11-33 U WITHOUT 97.5 1 × 10¹⁶ 250 Ge 14 10 1000 35 11-34 U WITHOUT 97.5 1 × 10¹⁶ 250 Ge 14 10 1000 35 11-35 U WITHOUT 97.5 1 × 10¹⁶ 250 Ge 14 10 1000 35 COMPARATIVE 11-36 U WITH 95 8 × 10¹⁶ 250 NONE 10 1000 17 EXAMPLE EXAMPLE 11-37 U WITH 95 8 × 10¹⁶ 250 Ge 14 10 1000 54 OF 11-38 U WITH 95 8 × 10¹⁶ 250 Ge 14 10 1000 54 PRESENT 11-39 U WITH 95 8 × 10¹⁶ 250 Ge 14 10 1000 54 INVENTION 11-40 U WITH 95 8 × 10¹⁶ 250 Ge 14 10 1000 54 11-41 U WITH 95 8 × 10¹⁶ 250 Ge 14 10 1000 54 11-42 U WITH 95 8 × 10¹⁶ 250 Ge 14 10 1000 54 FIRST SAMPLE SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION ACCUMULATION ACCUMULATION ACCUMULATION DEGREE OF KEEPING KEEPING DEGREE OF DEGREE OF COOLING DEGREE OF DEGREE OF CONDITION {222} PLANE TEMPERATURE TIME {200} PLANE {222} PLANE RATE DISTANCE {200} PLANE {222} PLANE No. (%) (° C.) (s) (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 11-1 13 1050 2 13 13 20 50 13 13 EXAMPLE EXAMPLE 11-2 17 1000 2 30 10 20 54 30 10 OF 11-3 17 1050 2 32 10 20 54 32 10 PRESENT 11-4 17 1050 5 32 10 20 54 32 10 INVENTION 11-5 17 1050 30 32 10 20 54 32 10 11-6 17 1050 120 32 10 20 54 32 10 11-7 17 1050 360 32 10 20 54 32 10 COMPARATIVE 11-8 13 1050 2 13 13 20 50 13 13 EXAMPLE EXAMPLE 11-9 9 1000 2 42 4.8 20 54 42 4.6 OF 11-10 9 1050 2 55 2.6 20 54 55 2.6 PRESENT 11-11 9 1050 5 55 2.6 20 54 55 2.6 INVENTION 11-12 9 1050 30 55 2.6 20 54 55 2.6 11-13 9 1050 120 55 2.6 20 54 55 2.6 11-14 9 1050 350 55 2.6 20 54 55 2.6 COMPARATIVE 11-15 13 1050 2 13 13 20 50 13 13 EXAMPLE EXAMPLE 11-16 2.1 1000 2 59 2.9 20 54 59 2.9 OF 11-17 2.1 1050 2 74 1.5 20 54 74 1.5 PRESENT 11-18 2.1 1050 5 74 1.5 20 54 74 1.5 INVENTION 11-19 2.1 1050 30 74 1.5 20 54 74 1.5 11-20 2.1 1050 120 74 1.5 20 54 74 1.5 11-21 2.1 1050 360 74 1.5 20 54 74 1.5 COMPARATIVE 11-22 13 1100 2 13 13 20 125 13 13 EXAMPLE EXAMPLE 11-23 15 1000 2 30 11 20 136 30 11 OF 11-24 15 1100 3 31 13 20 136 31 13 PRESENT 11-25 15 1100 7 31 13 20 136 31 13 INVENTION 11-26 15 1100 35 31 13 20 136 31 13 11-27 15 1100 140 31 13 20 136 31 13 11-28 15 1100 420 31 13 20 136 31 13 COMPARATIVE 11-29 14 1100 2 13 13 20 125 13 13 EXAMPLE EXAMPLE 11-30 8 1000 2 45 4.2 20 136 45 4.2 OF 11-31 8 1100 3 52 3.2 20 136 52 3.2 PRESENT 11-32 8 1100 7 52 3.2 20 136 52 3.2 INVENTION 11-33 8 1100 35 52 3.2 20 136 52 3.2 11-34 8 1100 140 52 3.2 20 136 52 3.2 11-35 8 1100 420 52 3.2 20 136 52 3.2 COMPARATIVE 11-36 12 1100 2 13 13 20 125 13 13 EXAMPLE EXAMPLE 11-37 3.4 1000 2 58 3 20 136 58 3 OF 11-38 3.4 1100 3 78 0.8 20 136 78 0.8 PRESENT 11-39 3.4 1100 7 78 0.8 20 136 78 0.8 INVENTION 11-40 3.4 1100 35 78 0.8 20 136 78 0.8 11-41 3.4 1100 140 78 0.8 20 136 78 0.8 11-42 3.4 1100 420 78 0.8 20 136 78 0.8

Further, an alloying ratio of the metal layer and a ratio of the α single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass % or less and the content of ferrite former was 99.5 mass % or more was regarded as an alloy layer. Further, a region where the Ga content was 4.1 mass % or more was regarded as the α single phase region, and a ratio of the α single phase region was found from the aforesaid expression (4). Results of these are listed in Table 27.

Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss W10/1 k (W10/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 27.

TABLE 27 RATIO OF ACCUMULATION ACCUMULATION ALLOYING α SINGLE DEGREE OF DEGREE OF CONDITION RATE PHASE {200} PLANE {222} PLANE B50 Bs B50/ W10/1k No. (%) (%) (%) (%) (T) (T) Bs (W/kg) COMPARATIVE 11-1 0 0 13 13 1.60 2.05 0.78 93 EXAMPLE EXAMPLE 11-2 5 0.1 30 10 1.74 2.05 0.85 63 OF 11-3 82 1.5 31 10 1.74 2.05 0.85 57 PRESENT 11-4 95 8.2 30 10 1.74 2.05 0.85 44 INVENTION 11-5 100 35 30 10 1.74 2.05 0.85 37 11-6 100 73 30 10 1.74 2.05 0.85 43 11-7 100 87 30 10 1.74 2.05 0.85 58 COMPARATIVE 11-8 0 0 13 13 1.60 2.05 0.78 92 EXAMPLE EXAMPLE 11-9 8 0.2 42 4.8 1.78 2.05 0.87 62 OF 11-10 64 2.6 53 2.7 1.85 2.05 0.90 57 PRESENT 11-11 94 7.8 53 2.7 1.87 2.05 0.91 42 INVENTION 11-12 100 42 53 2.7 1.85 2.05 0.90 33 11-13 100 71 53 2.7 1.85 2.05 0.90 38 11-14 100 95 53 2.7 1.87 2.05 0.91 53 COMPARATIVE 11-15 0 0 13 13 1.62 2.05 0.79 92 EXAMPLE EXAMPLE 11-16 5 0.2 59 2.9 1.87 2.05 0.91 63 OF 11-17 67 1.2 75 1.3 1.95 2.05 0.95 48 PRESENT 11-18 89 5.9 75 1.4 1.93 2.05 0.94 41 INVENTION 11-19 100 37 75 1.3 1.95 2.05 0.95 28 11-20 100 72 76 1.4 1.97 2.05 0.96 33 11-21 100 87 75 1.7 1.95 2.05 0.95 48 COMPARATIVE 11-22 0 0 13 13 1.60 2.05 0.78 101 EXAMPLE EXAMPLE 11-23 4 0.2 30 11 1.74 2.05 0.85 64 OF 11-24 57 1.2 32 9 1.74 2.05 0.85 56 PRESENT 11-25 87 6.7 32 9 1.74 2.05 0.85 45 INVENTION 11-26 100 45 32 9 1.74 2.05 0.85 37 11-27 100 72 32 9 1.74 2.05 0.85 42 11-28 100 92 32 9 1.74 2.05 0.85 57 COMPARATIVE 11-29 0 0 13 13 1.60 2.05 0.78 97 EXAMPLE EXAMPLE 11-30 9 0.4 45 4.2 1.80 2.05 0.88 63 OF 11-31 54 1.3 56 2.1 1.87 2.05 0.91 52 PRESENT 11-32 78 6.1 56 2.1 1.85 2.05 0.90 41 INVENTION 11-33 100 38 56 2.2 1.87 2.05 0.91 32 11-34 100 71 56 2.1 1.85 2.05 0.90 38 11-35 100 91 56 2.2 1.87 2.05 0.91 54 COMPARATIVE 11-36 0 0 13 13 1.62 2.05 0.79 100 EXAMPLE EXAMPLE 11-37 9 0.2 58 3 1.91 2.05 0.93 64 OF 11-38 70 2.3 82 0.8 1.95 2.05 0.95 48 PRESENT 11-39 91 7.1 82 0.8 1.95 2.05 0.95 40 INVENTION 11-40 100 41 82 0.8 1.97 2.05 0.96 26 11-41 100 76 82 0.8 1.95 2.05 0.95 32 11-42 100 100 82 0.8 1.97 2.05 0.96 48

As listed in Table 26, in examples of the present invention (conditions No. 11-2 to No. 11-7, No. 11-9 to No. 11-14, No. 11-16 to No. 11-21, No. 11-23 to No. 11-28, No. 11-30 to No. 11-35, No. 11-37 to No. 11-42), the accumulation degree of the {200} planes in the α phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 27, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were within the desirable ranges of the present invention. As listed in Table 27, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the α phase was 30% or more and the accumulation degree of the {222} planes in the α phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more.

In the examples of the present invention, when the ratio of the α single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss W10/1 k maintained a higher property level. Further, it could be confirmed that the core loss W10/1 k has a still better property level when the ratio of the α single phase region is not less than 5% nor more than 80%.

Twelfth Experiment

In a twelfth experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. 12-1 to condition No. 12-42) were studied.

Base metal plates (silicon steel plates) used in the twelfth experiment contained components of the composition V listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the twelfth experiment transformed to a γ single phase was 1000° C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 12-1 to the condition No. 12-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively.

Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 μm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 28.

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the α phase was within a 17% to 24% range in each of the base metal plates.

Thereafter, Ge layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by a sputtering method, except in the conditions No. 12-1, No. 12-8, No. 12-15, No. 12-22, No. 12-29, and No. 12-36. Thickness of each of the Ga layers (total thickness on the both surfaces) is listed in Table 28.

Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 28.

TABLE 28 FIRST SAMPLE BASE METAL PLATE ACCUMULATION REDUCTION DISLOCATION METAL LAYER HETING MEASURED DEGREE OF CONDITION RATE DENSITY THICKNESS THICKNESS RATE TEMPERATURE {200} PLANE No. COMPOSITION BLASTING (%) (m/m³) (μm) ELEMENT (μm) (° C./s) (° C.) (%) COMPARATIVE 12-1 V WITHOUT 95 1 × 10¹⁵ 100 NONE 10 1000 17 EXAMPLE EXAMPLE 12-2 V WITHOUT 95 1 × 10¹⁵ 100 Ge 7 10 1000 26 OF 12-3 V WITHOUT 95 1 × 10¹⁶ 100 Ge 7 10 1000 26 PRESENT 12-4 V WITHOUT 95 1 × 10¹⁵ 100 Ge 7 10 1000 26 INVENTION 12-5 V WITHOUT 95 1 × 10¹⁵ 100 Ge 7 10 1000 26 12-6 V WITHOUT 95 1 × 10¹⁵ 100 Ge 7 10 1000 26 12-7 V WITHOUT 95 1 × 10¹⁵ 100 Ge 7 10 1000 26 COMPARATIVE 12-8 V WITHOUT 97.5 1 × 10¹⁶ 100 NONE 10 1000 18 EXAMPLE EXAMPLE 12-9 V WITHOUT 97.5 1 × 10¹⁶ 100 Ge 7 10 1000 39 OF 12-10 V WITHOUT 97.5 1 × 10¹⁶ 100 Ge 7 10 1000 39 PRESENT 12-11 V WITHOUT 97.5 1 × 10¹⁶ 100 Ge 7 10 1000 39 INVENTION 12-12 V WITHOUT 97.5 1 × 10¹⁶ 100 Ge 7 10 1000 39 12-13 V WITHOUT 97.5 1 × 10¹⁶ 100 Ge 7 10 1000 39 12-14 V WITHOUT 97.5 1 × 10¹⁶ 100 Ge 7 10 1000 39 COMPARATIVE 12-15 V WITH 95 8 × 10¹⁶ 100 NONE 10 1000 17 EXAMPLE EXAMPLE 12-16 V WITH 95 8 × 10¹⁶ 100 Ge 7 10 1000 58 OF 12-17 V WITH 95 8 × 10¹⁶ 100 Ge 7 10 1000 58 PRESENT 12-18 V WITH 95 8 × 10¹⁶ 100 Ge 7 10 1000 58 INVENTION 12-19 V WITH 95 8 × 10¹⁶ 100 Ge 7 10 1000 58 12-20 V WITH 95 8 × 10¹⁶ 100 Ge 7 10 1000 58 12-21 V WITH 95 8 × 10¹⁶ 100 Ge 7 10 1000 58 COMPARATIVE 12-22 V WITHOUT 95 1 × 10¹⁵ 250 NONE 10 1000 17 EXAMPLE EXAMPLE 12-23 V WITHOUT 95 1 × 10¹⁵ 250 Ge 17 10 1000 27 OF 12-24 V WITHOUT 95 1 × 10¹⁵ 250 Ge 17 10 1000 27 PRESENT 12-25 V WITHOUT 95 1 × 10¹⁵ 250 Ge 17 10 1000 27 INVENTION 12-26 V WITHOUT 95 1 × 10¹⁵ 250 Ge 17 10 1000 27 12-27 V WITHOUT 95 1 × 10¹⁵ 250 Ge 17 10 1000 27 12-28 V WITHOUT 95 1 × 10¹⁵ 250 Ge 17 10 1000 27 COMPARATIVE 12-29 V WITHOUT 97.5 1 × 10¹⁶ 250 NONE 10 1000 16 EXAMPLE EXAMPLE 12-30 V WITHOUT 97.5 1 × 10¹⁶ 250 Ge 17 10 1000 42 OF 12-31 V WITHOUT 97.5 1 × 10¹⁶ 250 Ge 17 10 1000 42 PRESENT 12-32 V WITHOUT 97.5 1 × 10¹⁶ 250 Ge 17 10 1000 42 INVENTION 12-33 V WITHOUT 97.5 1 × 10¹⁶ 250 Ge 17 10 1000 42 12-34 V WITHOUT 97.5 1 × 10¹⁶ 250 Ge 17 10 1000 42 12-35 V WITHOUT 97.5 1 × 10¹⁶ 250 Ge I7 10 1000 42 COMPARATIVE 12-36 V WITH 95 8 × 10¹⁶ 250 NONE 10 1000 17 EXAMPLE EXAMPLE 12-37 V WITH 95 8 × 10¹⁶ 250 Ge 17 10 1000 50 OF 12-38 V WITH 95 8 × 10¹⁶ 250 Ge 17 10 1000 50 PRESENT 12-39 V WITH 95 8 × 10¹⁶ 250 Ge 17 10 1000 50 INVENTION 12-40 V WITH 95 8 × 10¹⁶ 250 Ge 17 10 1000 50 12-41 V WITH 95 8 × 10¹⁶ 250 Ge 17 10 1000 50 12-42 V WITH 95 8 × 10¹⁶ 250 Ge 17 10 1000 50 FIRST SAMPLE SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION ACCUMULATION ACCUMULATION ACCUMULATION DEGREE OF KEEPING KEEPING DEGREE OF DEGREE OF COOLING DEGREE OF DEGREE OF CONDITION {222} PLANE TEMPERATURE TIME {200} PLANE {222} PLANE RATE DISTANCE {200} PLANE {222} PLANE No. (%) (° C.) (s) (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 12-1 13 1100 2 13 13 15 50 13 13 EXAMPLE EXAMPLE 12-2 16 1000 2 30 11 15 54 30 11 OF 12-3 16 1100 2 30 12 15 54 30 12 PRESENT 12-4 16 1100 5 30 12 15 54 30 12 INVENTION 12-5 16 1100 30 30 12 15 54 30 12 12-6 16 1100 120 30 12 15 54 30 12 12-7 16 1100 360 30 12 15 54 30 12 COMPARATIVE 12-8 13 1100 2 13 13 15 50 13 13 EXAMPLE EXAMPLE 12-9 10 1000 2 42 4.9 15 54 42 4.9 OF 12-10 10 1100 2 55 2.8 15 54 55 2.8 PRESENT 12-11 10 1100 5 55 2.8 15 54 55 2.8 INVENTION 12-12 10 1100 30 55 2.8 15 54 55 2.8 12-13 10 1100 120 55 2.8 15 54 55 2.8 12-14 10 1100 360 55 2.8 15 54 55 2.8 COMPARATIVE 12-15 14 1100 2 13 13 15 50 13 13 EXAMPLE EXAMPLE 12-16 3.2 1000 2 61 2.4 15 54 61 2.4 OF 12-17 3.2 1100 2 77 1.3 15 54 77 1.3 PRESENT 12-18 3.2 1100 5 77 1.3 15 54 77 1.3 INVENTION 12-19 3.2 1100 30 77 1.3 15 54 77 1.3 12-20 3.2 1100 120 77 1.3 15 54 77 1.3 12-21 3.2 1100 360 77 1.3 15 54 77 1.3 COMPARATIVE 12-22 13 1150 2 13 13 15 125 13 13 EXAMPLE EXAMPLE 12-23 17 1000 2 30 10 15 136 30 10 OF 12-24 17 1150 3 32 14 15 136 32 14 PRESENT 12-25 17 1150 7 32 14 15 136 32 14 INVENTION 12-26 17 1150 35 32 14 15 136 32 14 12-27 17 1150 140 32 14 15 136 32 14 12-28 17 1150 420 32 14 15 136 32 14 COMPARATIVE 12-29 14 1150 2 13 13 15 125 13 13 EXAMPLE EXAMPLE 12-30 4 1000 2 43 4.9 15 136 43 4.9 OF 12-31 4 1150 3 59 1.8 15 136 59 1.8 PRESENT 12-32 4 1150 7 59 1.8 15 136 59 1.8 INVENTION 12-33 4 1150 35 59 1.8 15 136 59 1.6 12-34 4 1150 140 59 1.8 15 136 59 1.8 12-35 4 1150 420 59 1.8 15 136 59 1.8 COMPARATIVE 12-36 13 1150 2 13 13 15 125 13 13 EXAMPLE EXAMPLE 12-37 3.4 1000 2 58 2.8 15 136 58 2.8 OF 12-38 3.4 1150 3 79 0.8 15 136 79 0.8 PRESENT 12-39 3.4 1150 7 79 0.8 15 136 79 0.8 INVENTION 12-40 3.4 1150 35 79 0.8 15 136 79 0.8 12-41 3.4 1150 140 79 0.8 15 136 79 0.8 12-42 3.4 1150 420 79 0.8 15 136 70 0.8

Further, an alloying ratio of the metal layer and a ratio of an α single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass % or less and the content of ferrite former was 99.5 mass % or more was regarded as an alloy layer. Further, a region where the Ge content was 6.4 mass % or more was regarded as the α single phase region, and a ratio of the α single phase region was found from the aforesaid expression (4). Results of these are listed in Table 29.

Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss W10/1 k (W10/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 29.

TABLE 29 RATIO OF ACCUMULATION ACCUMULATION ALLOYING α SINGLE DEGREE OF DEGREE OF CONDITION RATE PHASE {200} PLANE {222} PLANE B50 Bs B50/ W10/1k No. (%) (%) (%) (%) (T) (T) Bs (W/kg) COMPARATIVE 12-1 0 0 13 13 1.60 2.05 0.78 94 EXAMPLE EXAMPLE 12-2 5 0.1 30 11 1.74 2.05 0.85 64 OF 12-3 82 1.5 31 10 1.74 2.05 0.85 57 PRESENT 12-4 95 8.2 30 10 1.74 2.05 0.85 44 INVENTION 12-5 100 35 30 10 1.74 2.05 0.85 37 12-6 100 73 30 10 1.74 2.05 0.85 43 12-7 100 87 30 10 1.74 2.05 0.85 58 COMPARATIVE 12-8 0 0 13 13 1.60 2.05 0.78 93 EXAMPLE EXAMPLE 12-9 7 0.2 42 4.9 1.82 2.05 0.89 62 OF 12-10 75 2.6 53 2.7 1.85 2.05 0.90 57 PRESENT 12-11 94 7.8 53 2.7 1.87 2.05 0.91 42 INVENTION 12-12 100 42 53 2.7 1.85 2.05 0.90 33 12-13 100 71 53 2.7 1.85 2.05 0.90 38 12-14 100 95 53 2.7 1.87 2.05 0.91 53 COMPARATIVE 12-15 0 0 13 13 1.62 2.05 0.79 95 EXAMPLE EXAMPLE 12-16 7 0.2 61 2.4 1.91 2.05 0.93 61 OF 12-17 67 1.2 75 1.3 1.95 2.05 0.95 48 PRESENT 12-18 89 5.9 75 1.4 1.93 2.05 0.94 41 INVENTION 12-19 100 37 75 1.3 1.95 2.05 0.95 28 12-20 100 72 76 1.4 1.97 2.05 0.96 33 12-21 100 87 75 1.7 1.95 2.05 0.95 48 COMPARATIVE 12-22 0 0 13 13 1.60 2.05 0.78 98 EXAMPLE EXAMPLE 12-23 10 0.3 30 10 1.74 2.05 0.85 64 OF 12-24 57 1.2 32 9 1.74 2.05 0.85 56 PRESENT 12-25 87 6.7 32 9 1.74 2.05 0.85 45 INVENTION 12-26 100 45 32 9 1.74 2.05 0.85 37 12-27 100 72 32 9 1.74 2.05 0.85 42 12-28 100 92 32 9 1.74 2.05 0.85 57 COMPARATIVE 12-29 0 0 13 13 1.60 2.05 0.78 104 EXAMPLE EXAMPLE 12-30 5 0.1 43 4.9 1.78 2.05 0.87 63 OF 12-31 54 1.3 56 2.1 1.87 2.05 0.91 52 PRESENT 12-32 78 6.1 56 2.1 1.85 2.05 0.90 41 INVENTION 12-33 100 38 56 2.2 1.87 2.05 0.91 32 12-34 100 71 56 2.1 1.85 2.05 0.90 38 12-35 100 91 56 2.2 1.87 2.05 0.91 54 COMPARATIVE 12-36 0 0 13 13 1.62 2.05 0.79 98 EXAMPLE EXAMPLE 12-37 6 0.3 58 2.8 1.89 2.05 0.92 63 OF 12-38 70 2.3 82 0.8 1.95 2.05 0.95 46 PRESENT 12-39 91 7.1 82 0.8 1.95 2.05 0.95 40 INVENTION 12-40 100 41 82 0.8 1.97 2.05 0.96 26 12-41 100 76 82 0.8 1.95 2.05 0.95 32 12-42 100 100 82 0.8 1.97 2.05 0.96 48

As listed in Table 28, in examples of the present invention (conditions No. 12-2 to No. 12-7, No. 12-9 to No. 12-14, No. 12-16 to No. 12-21, No. 12-23 to No. 12-28, No. 12-30 to No. 12-35, No. 12-37 to No. 12-42), the accumulation degree of the {200} planes in the α phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 29, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were within the desirable ranges of the present invention. As listed in Table 29, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200 } planes in the α phase was 30% or more and the accumulation degree of the {222} planes in the α phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more.

In the examples of the present invention, when the ratio of the α single phase region was 1% or more and the accumulation degree of the {200 } planes was 30% or more, not only the magnetic flux density B50 but also the core loss W10/1 k maintained a higher property level. Further, it could be confirmed that the core loss W10/1 k has a still better property level when the ratio of the α single phase region is not less than 5% nor more than 80%.

Thirteenth Experiment

In a thirteenth experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. 13-1 to condition No. 13-42) were studied.

Base metal plates (silicon steel plates) used in the thirteenth experiment contained components of the composition W listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the thirteenth experiment transformed to a γ single phase was 1010° C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 13-1 to the condition No. 13-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively.

Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 μm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 30.

Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an α phase. Further, the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured by the aforesaid method, it was found that, as rolled, the accumulation degree of the {200} planes in the α phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the α phase was within a 17% to 24% range in each of the base metal plates.

Thereafter, W layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by a sputtering method, except in the conditions No. 13-1, No. 13-8, No. 13-15, No. 13-22, No. 13-29, and No. 13-36. Thickness of each of the W layers (total thickness on the both surfaces) is listed in Table 30.

Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the α phase and the accumulation degree of the {222} planes in the α phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 30.

TABLE 30 FIRST SAMPLE BASE METAL PLATE ACCUMULATION REDUCTION DISLOCATION METAL LAYER HETING MEASURED DEGREE OF CONDITION RATE DENSITY THICKNESS THICKNESS RATE TEMPERATURE {200} PLANE No. COMPOSITION BLASTING (%) (m/m³) (μm) ELEMENT (μm) (° C./s) (° C.) (%) COMPARATIVE 13-1 W WITHOUT 95 1 × 10¹⁵ 100 NONE 5 1010 16 EXAMPLE EXAMPLE 13-2 W WITHOUT 95 1 × 10¹⁵ 100 W 1.2 5 1010 27 OF 13-3 W WITHOUT 95 1 × 10¹⁵ 100 W 1.2 5 1010 27 PRESENT 13-4 W WITHOUT 95 1 × 10¹⁵ 100 W 1.2 5 1010 27 INVENTION 13-5 W WITHOUT 95 1 × 10¹⁵ 100 W 1.2 5 1010 27 13-6 W WITHOUT 95 1 × 10¹⁵ 100 W 1.2 5 1010 27 13-7 W WITHOUT 95 1 × 10¹⁵ 100 W 1.2 5 1010 27 COMPARATIVE 13-8 W WITHOUT 97.5 1 × 10¹⁵ 100 NONE 5 1010 15 EXAMPLE EXAMPLE 13-9 W WITHOUT 97.5 1 × 10¹⁵ 100 W 1.2 5 1010 41 OF 13-10 W WITHOUT 97.5 1 × 10¹⁵ 100 W 1.2 5 1010 41 PRESENT 13-11 W WITHOUT 97.5 1 × 10¹⁵ 100 W 1.2 5 1010 41 INVENTION 13-12 W WITHOUT 97.5 1 × 10¹⁵ 100 W 1.2 5 1010 41 13-13 W WITHOUT 97.5 1 × 10¹⁵ 100 W 1.2 5 1010 41 13-14 W WITHOUT 97.5 1 × 10¹⁵ 100 W 1.2 5 1010 41 COMPARATIVE 13-15 W WITH 95 8 × 10¹⁶ 100 NONE 5 1010 15 EXAMPLE EXAMPLE 13-16 W WITH 95 8 × 10¹⁶ 100 W 1.2 5 1010 61 OF 13-17 W WITH 95 8 × 10¹⁶ 100 W 1.2 5 1010 61 PRESENT 13-18 W WITH 95 8 × 10¹⁶ 100 W 1.2 5 1010 61 INVENTION 13-19 W WITH 95 8 × 10¹⁶ 100 W 1.2 5 1010 61 13-20 W WITH 95 8 × 10¹⁶ 100 W 1.2 5 1010 61 13-21 W WITH 95 8 × 10¹⁶ 100 W 1.2 5 1010 61 COMPARATIVE 13-22 W WITHOUT 95 1 × 10¹⁵ 250 NONE 5 1010 15 EXAMPLE EXAMPLE 13-23 W WITHOUT 95 1 × 10¹⁵ 250 W 3 5 1010 26 OF 13-24 W WITHOUT 95 1 × 10¹⁵ 250 W 3 5 1010 26 PRESENT 13-25 W WITHOUT 95 1 × 10¹⁵ 250 W 3 5 1010 26 INVENTION 13-26 W WITHOUT 95 1 × 10¹⁵ 250 W 3 5 1010 26 13-27 W WITHOUT 95 1 × 10¹⁵ 250 W 3 5 1010 26 13-28 W WITHOUT 95 1 × 10¹⁵ 250 W 3 5 1010 26 COMPARATIVE 13-29 W WITHOUT 97.5 1 × 10¹⁵ 250 NONE 5 1010 15 EXAMPLE EXAMPLE 13-30 W WITHOUT 97.5 1 × 10¹⁵ 250 W 3 5 1010 37 OF 13-31 W WITHOUT 97.5 1 × 10¹⁵ 250 W 3 5 1010 37 PRESENT 13-32 W WITHOUT 97.5 1 × 10¹⁵ 250 W 3 5 1010 37 INVENTION 13-33 W WITHOUT 97.5 1 × 10¹⁵ 250 W 3 5 1010 37 13-34 W WITHOUT 97.5 1 × 10¹⁵ 250 W 3 5 1010 37 13-35 W WITHOUT 97.5 1 × 10¹⁵ 250 W 3 5 1010 37 COMPARATIVE 13-36 W WITH 95 8 × 10¹⁶ 250 NONE 5 1010 15 EXAMPLE EXAMPLE 13-37 W WITH 95 8 × 10¹⁶ 250 W 3 5 1010 58 OF 13-38 W WITH 95 8 × 10¹⁶ 250 W 3 5 1010 58 PRESENT 13-39 W WITH 95 8 × 10¹⁶ 250 W 3 5 1010 58 INVENTION 13-40 W WITH 95 8 × 10¹⁶ 250 W 3 5 1010 58 13-41 W WITH 95 8 × 10¹⁶ 250 W 3 5 1010 58 13-42 W WITH 95 8 × 10¹⁶ 250 W 3 5 1010 58 FIRST SAMPLE SECOND SAMPLE THIRD SAMPLE ACCUMULATION ACCUMULATION ACCUMULATION ACCUMULATION ACCUMULATION DEGREE OF KEEPING KEEPING DEGREE OF DEGREE OF COOLING DEGREE OF DEGREE OF CONDITION {222} PLANE TEMPERATURE TIME {200} PLANE {222} PLANE RATE DISTANCE {200} PLANE {222} PLANE No. (%) (° C.) (s) (%) (%) (° C./s) (μm) (%) (%) COMPARATIVE 13-1 14 1150 2 13 13 3 50 13 13 EXAMPLE EXAMPLE 13-2 12 1010 2 30 11 3 54 30 11 OF 13-3 12 1150 2 36 8 3 54 36 8 PRESENT 13-4 12 1150 5 36 8 3 54 36 8 INVENTION 13-5 12 1150 30 36 8 3 54 36 8 13-6 12 1150 120 36 8 3 54 36 8 13-7 12 1150 360 36 8 3 54 36 8 COMPARATIVE 13-8 13 1150 2 13 13 3 50 13 13 EXAMPLE EXAMPLE 13-9 8 1010 2 43 5.9 3 54 43 5.9 OF 13-10 8 1150 2 57 2.1 3 54 57 2.1 PRESENT 13-11 8 1150 5 57 2.1 3 54 57 2.1 INVENTION 13-12 8 1150 30 57 2.1 3 54 57 2.1 13-13 8 1150 120 57 2.1 3 54 57 2.1 13-14 8 1150 360 57 2.1 3 54 57 2.1 COMPARATIVE 13-15 13 1150 2 13 13 3 50 13 13 EXAMPLE EXAMPLE 13-16 2.8 1010 2 63 2 3 54 63 2 OF 13-17 2.8 1150 2 83 0.9 3 54 83 0.9 PRESENT 13-18 2.8 1150 5 83 0.9 3 54 83 0.9 INVENTION 13-19 2.8 1150 30 83 0.9 3 54 83 0.9 13-20 2.8 1150 120 83 0.9 3 54 83 0.9 13-21 2.8 1150 360 83 0.9 3 54 83 0.9 COMPARATIVE 13-22 13 1200 2 13 13 3 125 13 13 EXAMPLE EXAMPLE 13-23 13 1010 2 30 11 3 136 30 11 OF 13-24 13 1200 3 34 10 3 136 34 10 PRESENT 13-25 13 1200 7 34 10 3 136 34 10 INVENTION 13-26 13 1200 35 34 10 3 136 34 10 13-27 13 1200 140 34 10 3 136 34 10 13-28 13 1200 420 34 10 3 136 34 10 COMPARATIVE 13-29 14 1200 2 13 13 3 125 13 13 EXAMPLE EXAMPLE 13-30 10 1000 2 41 5.3 3 136 41 5.3 OF 13-31 10 1200 3 55 2.5 3 136 55 2.8 PRESENT 13-32 10 1200 7 55 2.8 3 136 55 2.8 INVENTION 13-33 10 1200 35 55 2.8 3 136 55 2.8 13-34 10 1200 140 55 2.8 3 136 55 2.8 13-35 10 1200 420 55 2.8 3 136 55 2.8 COMPARATIVE 13-36 14 1200 2 13 13 3 125 13 13 EXAMPLE EXAMPLE 13-37 3.2 1010 2 60 2.5 3 136 60 2.5 OF 13-38 3.2 1200 3 82 0.8 3 136 82 0.8 PRESENT 13-39 3.2 1200 7 82 0.8 3 136 82 0.8 INVENTION 13-40 3.2 1200 35 82 0.8 3 136 82 0.8 13-41 3.2 1200 140 82 0.8 3 136 82 0.8 13-42 3.2 1200 420 82 0.8 3 136 82 0.8

Further, an alloying ratio of the metal layer and a ratio of an α single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass % or less and the content of ferrite former was 99.5 mass % or more was regarded as an alloy layer. Further, a region where the W content was 6.6 mass % or more was regarded as the α single phase region, and a ratio of the α single phase region was found from the aforesaid expression (4). Results of these are listed in Table 31.

Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss W10/1 k (W10/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 31.

TABLE 31 RATIO OF ACCUMULATION ACCUMULATION ALLOYING α SINGLE DEGREE OF DEGREE OF CONDITION RATE PHASE {200} PLANE {222} PLANE B50 Bs B50/ W10/1k No. (%) (%) (%) (%) (T) (T) Bs (W/kg) COMPARATIVE 13-1 0 0 13 13 1.60 2.05 0.78 91 EXAMPLE EXAMPLE 13-2 7 0.2 30 11 1.74 2.05 0.85 63 OF 13-3 82 1.5 31 10 1.74 2.05 0.85 57 PRESENT 13-4 95 8.2 30 10 1.74 2.05 0.85 44 INVENTION 13-5 100 35 30 10 1.74 2.05 0.85 37 13-6 100 73 30 10 1.74 2.05 0.85 43 13-7 100 87 30 10 1.74 2.05 0.85 58 COMPARATIVE 13-8 0 0 13 13 1.60 2.05 0.78 92 EXAMPLE EXAMPLE 13-9 10 0.3 43 5.9 1.78 2.05 0.87 61 OF 13-10 64 2.6 53 2.7 1.85 2.05 0.90 57 PRESENT 13-11 94 7.8 53 2.7 1.87 2.05 0.91 42 INVENTION 13-12 100 42 53 2.7 1.85 2.05 0.90 33 13-13 100 71 53 2.7 1.85 2.05 0.90 38 13-14 100 95 53 2.7 1.87 2.05 0.91 53 COMPARATIVE 13-15 0 0 13 13 1.62 2.05 0.79 92 EXAMPLE EXAMPLE 13-16 5 0.1 63 2 1.91 2.05 0.93 63 OF 13-17 67 1.2 75 1.3 1.95 2.05 0.95 48 PRESENT 13-18 89 5.9 75 1.4 1.93 2.05 0.94 41 INVENTION 13-19 100 37 75 1.3 1.95 2.05 0.95 28 13-20 100 72 76 1.4 1.97 2.05 0.96 33 13-21 100 87 75 1.7 1.95 2.05 0.95 48 COMPARATIVE 13-22 0 0 13 13 1.60 2.05 0.78 99 EXAMPLE EXAMPLE 13-23 8 0.3 30 11 1.74 2.05 0.85 64 OF 13-24 57 1.2 32 9 1.74 2.05 0.85 56 PRESENT 13-25 87 6.7 32 9 1.74 2.05 0.85 45 INVENTION 13-26 100 45 32 9 1.74 2.05 0.85 37 13-27 100 72 32 9 1.74 2.05 0.85 42 13-28 100 92 32 9 1.74 2.05 0.85 57 COMPARATIVE 13-29 0 0 13 13 1.60 2.05 0.78 101 EXAMPLE EXAMPLE 13-30 8 0.3 41 5.3 1.78 2.05 0.87 64 OF 13-31 54 1.3 56 2.1 1.87 2.05 0.91 52 PRESENT 13-32 78 6.1 56 2.1 1.85 2.05 0.90 41 INVENTION 13-33 100 38 56 2.2 1.87 2.05 0.91 32 13-34 100 71 56 2.1 1.85 2.05 0.90 38 13-35 100 91 56 2.2 1.87 2.05 0.91 54 COMPARATIVE 13-36 0 0 13 13 1.62 2.05 0.79 102 EXAMPLE EXAMPLE 13-37 8 0.2 60 2.5 1.89 2.05 0.92 63 OF 13-38 70 2.3 82 0.8 1.95 2.05 0.95 46 PRESENT 13-39 91 7.1 82 0.8 1.95 2.05 0.95 40 INVENTION 13-40 100 41 82 0.8 1.97 2.05 0.96 26 13-41 100 76 82 0.8 1.95 2.05 0.95 32 13-42 100 100 82 0.8 1.97 2.05 0.96 48

As listed in Table 30, in examples of the present invention (conditions No. 13-2 to No. 13-7, No. 13-9 to No. 13-14, No. 13-16 to No. 13-21, No. 13-23 to No. 13-28, No. 13-30 to No. 13-35, No. 13-37 to No. 13-42), the accumulation degree of the {200} planes in the α phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 31, in the examples of the present invention, the alloying ratio and the ratio of the α single phase region were within the desirable ranges of the present invention. As listed in Table 31, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the α phase was 30% or more and the accumulation degree of the {222} planes in the α phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more.

In the examples of the present invention, when the ratio of the α single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss W10/1 k maintained a higher property level. Further, it could be confirmed that the core loss W10/1 k has a still better property level when the ratio of the α single phase region is not less than 5% nor more than 80%.

INDUSTRIAL APPLICABILITY

The present invention is usable in, for example, industries related to magnetic materials such as iron cores. 

The invention claimed is:
 1. A method of manufacturing an Fe-based metal plate comprising: forming a metal layer containing ferrite former on at least one surface of a base metal plate of an α-γ transforming Fe or Fe alloy; next heating the base metal plate and the metal layer to an A3 point of the Fe or the Fe alloy so as to diffuse the ferrite former into the base metal plate and form an alloy region of a ferrite phase in which an accumulation degree of {200} planes is 25% or more and an accumulation degree of {222} planes is 40% or less; and next heating the base metal plate to a temperature equal to or higher than the A3 point of the Fe or the Fe alloy so as to increase the accumulation degree of the {200} planes and decrease the accumulation degree of the {222} planes while maintaining the alloy region of the ferrite phase.
 2. The method of manufacturing an Fe-based metal plate according to claim 1, comprising, after the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, cooling the base metal plate to a temperature lower than the A3 point of the Fe or the Fe alloy so as to transform an unalloyed region in the base metal plate from an austenitic phase to a ferrite phase, further increase the accumulation degree of the {200} planes and further decrease the accumulation degree of the {222} planes.
 3. The method of manufacturing an Fe-based metal plate according to claim 1, wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, the accumulation degree of the {200} planes is increased to 30% or more and the accumulation degree of the {222} planes is decreased to 30% or less.
 4. The method of manufacturing an Fe-based metal plate according to claim 1, wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, the accumulation degree of the {200} planes is increased to 50% or more and the accumulation degree of the {222} planes is decreased to 15% or less.
 5. The method of manufacturing an Fe-based metal plate according to claim 1, wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, the ferrite former contained in the metal layer are all diffused into the base metal plate.
 6. The method of manufacturing an Fe-based metal plate according to claim 1, wherein the ferrite former are at least one kind selected from a group consisting of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ti, V, W, and Zn.
 7. The method of manufacturing an Fe-based metal plate according to claim 1, wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, an area ratio of a ferrite single phase region to the metal plate in a cross section in a thickness direction is made to 1% or more.
 8. The method of manufacturing an Fe-based metal plate according to claim 1, wherein as the base metal plate, used is one in which a working strain is brought about and in which dislocation density is not less than 1×10¹⁵ m/m³ nor more than 1 ×10¹⁷ m/m³.
 9. The method of manufacturing an Fe-based metal plate according to claim 1, wherein as the base metal plate, used is one in which a working strain is brought about by cold rolling in which rolling reduction ratio is not less than 97% nor more than 99.99%.
 10. The method of manufacturing an Fe-based metal plate according to claim 1, wherein as the base metal plate, used is one in which a working strain is brought about by shot blasting.
 11. The method of manufacturing an Fe-based metal plate according to claim 1, wherein as the base metal plate, used is one in which a working strain is brought about by cold rolling in which rolling reduction ratio is not less than 50% nor more than 99.99% and shot blasting.
 12. The method of manufacturing an Fe-based metal plate according to claim 1, wherein as the base metal plate, used is one in which a shear strain of 0.2 or more is brought about by cold rolling.
 13. The method of manufacturing an Fe-based metal plate according to claim 1, wherein as the base metal plate, used is one in which a shear strain of 0.1 or more is brought about by cold rolling and a working strain is brought about by shot blasting.
 14. The method of manufacturing an Fe-based metal plate according to claim 1, wherein a thickness of the base metal plate is not less than 10 μm nor more than 5 mm.
 15. A Fe-based metal plate, containing ferrite former, wherein, in a surface, an accumulation degree of {200} planes in a ferrite phase is 30% or more and an accumulation degree of {222} planes in the ferrite phase is 30% or less, and the ferrite former is at least one selected from the group consisting of Al, Cr, Ga, Ge, Mo, Sb, Sn, Ti, V, W and Zn, wherein the Fe-based metal plate is formed by diffusion of the ferrite former from a surface to an inner part of an α-γ transforming Fe or Fe alloy plate, and wherein a ratio of an α single phase region to the Fe-based metal plate in a thickness direction is not less than 5% and not more than 80%.
 16. The Fe-based metal plate according to claim 15, comprising, on the surface, a metal layer containing the ferrite former.
 17. The Fe-based metal plate according to claim 15, wherein the accumulation degree of the {200} planes is 50% or more and the accumulation degree of the {222} planes is 15% or less.
 18. The Fe-based metal plate according to claim 15, wherein the ferrite former are at least one kind selected from a group consisting of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ti, V, W, and Zn.
 19. The Fe-based metal plate according to claim 15, comprising a 1% ferrite single phase region or more in terms of an area ratio in a thicknesswise cross section of the metal plate. 